JPS59179719A - Manufacture of turbine rotor - Google Patents
Manufacture of turbine rotorInfo
- Publication number
- JPS59179719A JPS59179719A JP58053784A JP5378483A JPS59179719A JP S59179719 A JPS59179719 A JP S59179719A JP 58053784 A JP58053784 A JP 58053784A JP 5378483 A JP5378483 A JP 5378483A JP S59179719 A JPS59179719 A JP S59179719A
- Authority
- JP
- Japan
- Prior art keywords
- turbine rotor
- creep rupture
- rupture strength
- toughness
- temperature
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
〔発明の技術分野〕
この発明は高温で優れたクリープ破断強さを有する１Ｚ
ｃｒ系耐熱輸で侮成されたタービンロータの製造方法に
関する。[Detailed Description of the Invention] [Technical Field of the Invention] The present invention relates to a 1Z resin having excellent creep rupture strength at high temperatures.
This invention relates to a method for manufacturing a turbine rotor made of Cr-based heat-resistant material.
近年蒸気タービンやガスタービンは熱効率の向上を目的
に、使用する蒸気温度やガス温度か上昇してきている。In recent years, the steam and gas temperatures used in steam turbines and gas turbines have been increasing in order to improve their thermal efficiency.
ところで、クリープ破断強さの優れたロータの一つに１
２Ｃｒ−Ｍｏ−Ｖ−Ｎｂ（Ｔａ）−Ｎ Ｎで肩（成され
たロータカ；あるが、今後の高温化に対処するためには
〜１１こ尚温のクリープ破断強さに優れだ１２ｃｒ糸ロ
ーター必要とされる。By the way, one of the rotors with excellent creep rupture strength is 1.
2Cr-Mo-V-Nb(Ta)-N There is a rotor made of N, but in order to cope with future high temperatures, a 12cr yarn rotor with excellent creep rupture strength of ~11% is needed. Needed.
高温のクリープ破断強さ全同上させる方法の一つとして
焼入温度の上昇があるか、従来の１２Ｃｒ糸ロータで行
なわれている高周波炉や′セ弧炉による溶解で製造され
たタービンロータ素体の焼入温度をただ単に上昇させた
場合にはクリープ破断強さは向上するが、反曲延性・靭
性が低下し、−また切欠弱イヒを生じやすくなる。その
ためタービンロータのＩ范性破見に対する安全性信頼性
の観点より従来１２Ｃｒ系ターヒンロータの焼入温度は
クリープ破断強さと延性および靭怜已を考慮して１０３
０’０以上〜１０７０°Ｃ未満で行なっている。One way to increase the high-temperature creep rupture strength is to increase the quenching temperature, or to improve the turbine rotor body manufactured by melting in a high-frequency furnace or a 'cerc furnace', which is done with conventional 12Cr yarn rotors. If the quenching temperature is simply increased, the creep rupture strength will improve, but the reverse bending ductility and toughness will decrease, and notch damage will likely occur. Therefore, from the viewpoint of safety and reliability against I-flexure fracture of the turbine rotor, the quenching temperature of the conventional 12Cr-based Tahin rotor was set at 103°C in consideration of creep rupture strength, ductility, and toughness.
The temperature is 0'0 or more and less than 1070°C.
本発明は上記点に鑑みてなされたもので、高温のクリー
プ破断強さが優れるとともに延性および靭性にも優れた
タービンロータの脆性破壊に対する安全性、信頼性の高
い１２Ｃｒ系タービンロータの製造方法を提供すること
を目的としたものである。The present invention has been made in view of the above points, and provides a method for manufacturing a 12Cr-based turbine rotor that has excellent high-temperature creep rupture strength, excellent ductility and toughness, and has high safety and reliability against brittle fracture of the turbine rotor. It is intended to provide.
本発明は従来の１２ｃｒ系タービンロータの化学組成、
溶解方法および熱処理方法などについて広範凹に実験検
討した結果、高温のクリープ破断強さに優れ、かつ延性
および靭性にも優れだ１２Ｃｒ系タービンロータが得ら
れることを見いだした事による。The present invention discloses the chemical composition of a conventional 12cr turbine rotor,
As a result of extensive experimental studies on melting methods, heat treatment methods, etc., it was discovered that a 12Cr-based turbine rotor can be obtained that has excellent high-temperature creep rupture strength, as well as excellent ductility and toughness.
すなわち、本発明に係る１２Ｃｒ系タービンロータは重
量パーセントで００．１〜０．２５乞Ｓｉ［，５％以下
、Ｍｎ ０．１〜１．０％、Ｎｉ ０．１〜１．０ ％
、＋ Ｃｒ・・９ニド１＋３．Ｑ ％、Ｍ。That is, the 12Cr-based turbine rotor according to the present invention has a weight percentage of 0.1 to 0.25%, Si[, 5% or less, Mn 0.1 to 1.0%, and Ni 0.1 to 1.0%.
, + Cr..9 Nido 1+3. Q%, M.
０．５〜２．０％、Ｖｏ、１〜０．３’％、Ｎｂ、Ｔａ
の少なくとも一種０．０３〜０．３％、Ｎ Ｏ，０３〜
０．１ ％、残部Ｆｅおよび付随的不純物より成る合金
組成を有し、エレクトロスラグ再溶解による二次溶解を
して得得た鋼塊を鍛造成形してタービンロータ索体とし
たのち、１０９５°０以上〜１ｊ５０°ＣＪ）下の温度
範、囲に加熱後焼入れし、次いで５３０−７３００の温
度範囲で焼戻し処理を行うことを前像とする高温クリー
プ破断強さと延性および靭性に優れた１２Ｃｒ系タービ
ンロータの製造方法である。0.5-2.0%, Vo, 1-0.3'%, Nb, Ta
at least one kind of 0.03 to 0.3%, N O,03 to
A steel ingot having an alloy composition of 0.1%, the balance being Fe and incidental impurities, obtained by secondary melting by electroslag remelting, was forged to form a turbine rotor cable body, and then heated at 1095°. 12Cr system with excellent high-temperature creep rupture strength, ductility and toughness, which is heated to a temperature range of 0 to 1j50°CJ), then quenched, and then tempered in a temperature range of 530-7300°C. This is a method for manufacturing a turbine rotor.
ここで本発明方法に係る１ＺＣｒ系クービンロータの組
成および溶解、熱処理の限定理由Ｖこついて説明する。Here, the reason for limiting the composition, melting, and heat treatment of the 1ZCr Kubin rotor according to the method of the present invention will be explained.
Ｃは引張強さやクリープ破断「速さを確保するために必
要な元素であり、０１％未満ではフェライト相が生成し
てＰ９Ｔ要の特性が得られず、捷た０、２５チを越える
と靭性が低下することからこの範囲とする。C is an element necessary to ensure tensile strength and creep rupture speed; if it is less than 0.01%, a ferrite phase will form and the required properties of P9T cannot be obtained, and if it exceeds 0.25%, the toughness will decrease. It is set in this range because of the decrease in
Ｓｔは脱酸剤として添加する元素であるが多す−の添加
は靭性を劣下させるので０．５係以下とする。St is an element added as a deoxidizing agent, but since adding too much St will degrade toughness, it should be kept at a factor of 0.5 or less.
胤は脱酸、脱硫剤として添加する元素で０１％未満では
十分な効果得られず、また１０チを越えるとクリープ破
断強ざを低下させるのでこの範囲とする。Seed is an element added as a deoxidizing and desulfurizing agent, and if it is less than 10%, a sufficient effect cannot be obtained, and if it exceeds 10%, the creep rupture strength will decrease, so it is set within this range.
Ｎｉはフェライト相の生成を抑え均一なマルテンザイト
組社を得るために必要な元素であるが、Ｏ１１チ満では
その効果が発揮されに＜＜、また１、０襲を越えるとク
リープ破断師さを低下させるのでこのゆ１Σ囲とする。Ni is a necessary element to suppress the formation of ferrite phase and obtain a uniform martenzite structure, but if the O concentration is less than 11, its effect is not exhibited, and if it exceeds 1 or 0, it becomes a creep rupture breaker. Since this reduces the
なおＮｉの一部あるいは全部をＣｏＫ置き換えることは
可能である。Note that it is possible to replace part or all of Ni with CoK.
Ｃｒは本発明に係るロータの機械的性質ケ得るために必
要な元素で、その量が９０％未満では必要とするクリー
プ破断強きが確保し難く、また１３．０チを越えるとフ
ェライト相が生成し、クリープ破断強さが低下すること
からこの範囲とする。Cr is an element necessary to obtain the mechanical properties of the rotor according to the present invention. If the amount is less than 90%, it is difficult to secure the required creep rupture strength, and if it exceeds 13.0%, a ferrite phase is formed. However, since the creep rupture strength decreases, this range is set.
Ｍｏはクリープ破断強さの向上と焼戻し脱性を防止する
ために必要な元素で、０．５％未満ではその効果が十分
でなく、また２、０％を越えるとフェライト相の生成に
よるクリープ破断強さの低下や靭性の低下などを生ずる
ことからこの範囲とする。Mo is an element necessary to improve creep rupture strength and prevent detempering. If it is less than 0.5%, the effect will not be sufficient, and if it exceeds 2.0%, creep rupture will occur due to the formation of ferrite phase. This range is set because it causes a decrease in strength and toughness.
■はクリープ破断強さの向上に必要な元素であるが０．
１％未満ではその効果が十分でなく、また０゜３チを越
るとＩＶｌｏと同様にフェライト相が生成しクリープ破
断強さを低下させることφ）らこの範囲とする。■ is an element necessary for improving creep rupture strength, but 0.
If it is less than 1%, the effect will not be sufficient, and if it exceeds 0°3, a ferrite phase will be formed like IVlo, reducing the creep rupture strength (φ), so this range is set.
ＮｂおよびＴａは本発明に１，１りるロータをイ１１成
する１２Ｃｒ系鋼の素地中に炭ｒ化物としてｒ＆ Ａ１
１ｌｌに析出分散し、クリープ破断強さを１１】」上ざ
ぜるノ〔素で、その景が０．０３％未満では十分なく、
已、ミが創られず、吐た０、３％を越えると後述するエ
レクトロスラグ再溶解を行なってもロータ中心部に粗大
な炭（，５′ｊ化物を生成して延性を劣下させることか
らこのΩ囲とする。なお、さらに優れたクリープ破断’
ｊ：Ｇさを必要とする場合には、Ｎｂ、Ｔａの少なくと
も一種が０．１３％以上が望ましい。Nb and Ta are added as carbides in the matrix of 12Cr steel that forms the rotor of the present invention.
Precipitated and dispersed in 1 liter, the creep rupture strength is increased to 11%.
However, if the amount exceeds 0.3%, coarse charcoal (,5'j) will be formed in the center of the rotor, reducing ductility even if electroslag is remelted as described below. and this Ω range.In addition, even better creep rupture '
When j:G is required, it is desirable that at least one of Nb and Ta be 0.13% or more.
Ｎはフェライト相の生成を抑えるとともに炭窒化物を生
成してクリープ破断強さを向上させるに必要な元素で０
．０３％未満ではその効果が十分でなく、丑だ０．１チ
を越えるとピンホールやブローホール’ｃ 発生させる
ことからこの範囲としだ。N is an element necessary to suppress the formation of ferrite phase and to generate carbonitrides to improve creep rupture strength.
．． If it is less than 0.3%, the effect will not be sufficient, and if it exceeds 0.1%, pinholes or blowholes will occur, so this range is recommended.
次に本発明方法で重要なエレクトロスラグ再溶解および
熱処理について述べる。Next, electroslag remelting and heat treatment, which are important in the method of the present invention, will be described.
エレクトロスラグ再溶解を行う理由は、篩隠りリープ破
断強さ、延性および靭性に役れた１２Ｃｒ系タービンロ
ータを得るために、次に述べる熱処理と共に必要不可欠
な工程で、このエレクトロスラグ再溶解をしない従来の
高周波炉溶解や電弧炉溶解の瞥まの場合には焼入温度を
従来の１０５０ ’（３く±２０’Ｃ，最高で１０９０
℃よシ上昇した本発明方法と同じ焼入温ｇ１０９５°０
以上〜］、１５０℃以下で焼入すると、高温のクリープ
破断強さは同じような値になるが、延性や靭性が大幅に
低下し、脆性破壊に対する安全性や信頼性のある１２Ｃ
ｒ系タービンロータを得ることが出来ない。The reason for electroslag remelting is that in order to obtain a 12Cr-based turbine rotor with improved sieve leap rupture strength, ductility, and toughness, electroslag remelting is an essential step along with the heat treatment described below. In the case of conventional high frequency furnace melting or electric arc furnace melting, the quenching temperature should be changed to the conventional 1050' (3 ± 20'C, maximum 1090 °C).
The same quenching temperature as the method of the present invention, which is higher than ℃ 1095°0
If quenched at 150°C or lower, the high-temperature creep rupture strength will be similar, but the ductility and toughness will be significantly lower than 12C, which is safer and more reliable against brittle fracture.
It is not possible to obtain an r-series turbine rotor.
また、従来の１２Ｃｒ系タービンロータでは高周波溶解
炉や電弧炉で溶解した溶湯を鋳型に流し込み凝固させて
いるため溶湯の凝固に時間がかかり、タービンロータの
中心部にＮｂやＴａを含む粗大な炭窒化物が析出して靭
性の低下をまねくことからこれまでＮｂ ＋Ｔａの含有
量は通常０．０３〜０．１％程度までしか添加しておら
ず本発明方法によればそれ以上の添加でもクービンロー
タ中心部に炭化物の粗大偏析はなく、高温クリープ破断
強さに優れ、かつ延性や靭性にも優れた１２Ｃｒ系ター
ビンロータを得ることが出来る。１０９５（ｊＪＪ上〜
１１５０’Ｃ以下の温度範囲に加熱後焼入し、次いで５
３０〜７３０℃の温度範囲で焼戻しを行なう理由として
はＮｂやＴａの炭窒化物を多量に固溶させ焼戻しで再析
出させるには焼入れ温度が１０９５’Ｃ！未満では十分
でなく、また１１５０℃を越えると結晶粒の粗大化が大
きくなり、靭性を害するのでこの範囲とした。In addition, in conventional 12Cr turbine rotors, molten metal melted in a high-frequency melting furnace or electric arc furnace is poured into a mold and solidified, so it takes time to solidify the molten metal, and coarse carbon containing Nb and Ta is deposited in the center of the turbine rotor. Since nitrides precipitate and lead to a decrease in toughness, the content of Nb + Ta has conventionally been added to only about 0.03 to 0.1%, but according to the method of the present invention, even if more than that is added, the Kubin rotor It is possible to obtain a 12Cr-based turbine rotor with no coarse segregation of carbides in the center, excellent high-temperature creep rupture strength, and excellent ductility and toughness. 1095 (jJJ top~
After heating to a temperature range of 1150'C or less, quenching, then 5
The reason why tempering is performed in the temperature range of 30 to 730°C is that the quenching temperature is 1095'C to dissolve a large amount of Nb and Ta carbonitrides into solid solution and re-precipitate them during tempering! If it is less than 1150°C, it is not sufficient, and if it exceeds 1150°C, the crystal grains will become coarser and the toughness will be impaired, so this range was set.
また、焼戻し温度が５３０°Ｃ未満では十分な焼戻しが
行なわれず、所要の靭性が得られず、７３０’０を越え
た場合には所要の引張強さや耐力を得ることが出来ない
ことからこのづ・ａ囲とした。In addition, if the tempering temperature is less than 530°C, sufficient tempering will not be performed and the required toughness will not be obtained, and if the tempering temperature exceeds 730'0, the required tensile strength and yield strength cannot be obtained.・It was set as a circle.
なお、本発明方法に係るタービンロータの製造方法にお
いて上記エレクトロスラグ再溶解と熱処理の両者が必要
不可欠であシ、このうちの一つでも欠けた場合には高温
のクリープ破断強さに優れ、かつ延性および靭性を有す
る１２Ｃｒ系タービンロータを得ることは出来ない。In addition, in the method for manufacturing a turbine rotor according to the method of the present invention, both the electroslag remelting and heat treatment described above are indispensable, and if even one of them is lacking, it is necessary to have excellent high-temperature creep rupture strength and It is not possible to obtain a 12Cr-based turbine rotor with ductility and toughness.
〔発明の実施例〕
第１表に示す化学組成を石するタービンロータモデル（
直径６００ミリ、長さ８００ミリ）を作製したのち各種
試験を行なった。[Embodiments of the Invention] A turbine rotor model with the chemical composition shown in Table 1 (
After fabricating a specimen with a diameter of 600 mm and a length of 800 mm, various tests were conducted.
本発明に係る実施例１．２．３のタービンロータモデル
の作成は第１表に示した合金組成となるように原料を配
合したのち電弧炉で溶解次いでエレクトロスラグ再溶解
の消耗電極用モールドに鋳込みインゴットを得た。引続
いて、このインゴットを消耗電極としてエレクトロスラ
グ再溶解を行なっタッチ、鍛造を行ないタービンローｐ
モデル素体を得た。さらにこのタービンロータモデル
素体に第１表に併記した熱処理を施こしたのち機械加工
を行ないタービンロータモデルを得た。The turbine rotor model of Example 1.2.3 according to the present invention was created by mixing the raw materials to have the alloy composition shown in Table 1, melting them in an electric arc furnace, and then molding them into a mold for consumable electrodes for electroslag remelting. A cast ingot was obtained. Subsequently, this ingot was used as a consumable electrode by electroslag remelting, touch, and forging to form a turbine rope.
Obtained a model body. Furthermore, this turbine rotor model body was subjected to the heat treatment listed in Table 1 and then machined to obtain a turbine rotor model.
まだ、比較例１は上記実施例と同様に溶解、鍛造を行な
ったのち、第１表に併記した従来より行なわれている熱
処理を施こしたのち、機械加工を行ないタービンロータ
モデルを得た。However, in Comparative Example 1, after melting and forging in the same manner as in the above-mentioned Examples, a conventional heat treatment listed in Table 1 was performed, and then machining was performed to obtain a turbine rotor model.
さらに比較例２，３は従来の１２Ｃｒ系タービンロータ
の溶解方法と同様に電弧炉−で溶解した溶湯をモールド
に注ぎ、インゴットを得たのち、これを鍛造してタービ
ンロータモデル素体としたあと、第１表に併記しだ熱処
理、比較例２は従来より行なわれている熱処理、比較例
３は焼入温度を高くしだ熱処理を施こしたのち、機械加
工を行ないタービンロータモデルとした。Furthermore, in Comparative Examples 2 and 3, the molten metal melted in an electric arc furnace was poured into a mold in the same manner as the conventional melting method for 12Cr-based turbine rotors. After obtaining an ingot, this was forged to form a turbine rotor model body. , Comparative Example 2 was heat treated as shown in Table 1. Comparative Example 3 was heat treated at a higher quenching temperature, and then machined to form a turbine rotor model.
試験は上記のようにして得たタービンロータモデルのそ
れぞれについて試験片を切り出し、引張試験、衝撃試験
、クリープ破断試験を行なった。For testing, test pieces were cut out for each of the turbine rotor models obtained as described above, and a tensile test, an impact test, and a creep rupture test were conducted.
第２表に引張試験および衝撃試験結果をまた第３表にク
リープ破断試験結果を示す。Table 2 shows the results of the tensile test and impact test, and Table 3 shows the results of the creep rupture test.
以下余白
第２表および第３表より明らかなように、本発明方法に
係る１２Ｃｒ系クービンロータモデルは比較例に比べ引
張強さが優れるとともに伸ひ、絞りも太きく、゛また衝
撃靭性が著しく大きい。さらにクリープ破断強さも従来
の１２Ｃｒ系ロータ相でめる比較例２に比べるとりＩＪ
−プ４ｉ１１ｆｊｉ伸びや絞りは同等以上でありまたク
リープ破断強さも優れている。これらのことから本発明
方法に係る１２Ｃｒ系タービンロータ材は、罠温および
高温頻度に優れるとともに延性、り性にもイ受れており
工業上Ｍ ）［Ｊである。As is clear from Tables 2 and 3 below, the 12Cr-based Kubin rotor model according to the method of the present invention has superior tensile strength, elongation, and larger aperture compared to the comparative example, and also has poor impact toughness. significantly larger. Furthermore, the creep rupture strength is also higher than that of Comparative Example 2 using the conventional 12Cr rotor phase.
-P4i11fji The elongation and reduction of area are the same or higher, and the creep rupture strength is also excellent. From these facts, the 12Cr-based turbine rotor material according to the method of the present invention is excellent in trap temperature and high temperature frequency, and is also poor in ductility and stiffness, and is industrially rated M)[J.
代理人 弁理士 則 近 冠 佑 （ほか１名）Agent: Patent Attorney Noriyuki Chikan (1 other person)
Claims (1)
．５係以下、Ｍｎ ０．１〜１．０ ％、Ｎｉ Ｏ，１
〜１．０ ％、Ｃｒ ９．０〜１３．０ ％ｂ Ｍｏ
Ｏ，５〜２．０ ％、 Ｖ Ｏ，１〜０．３ ％、 Ｎ
ｂ 、Ｔａの少なくとも一種０．０３〜０．３％、ＮＯ
，０３〜０．１チ、残部Ｆｅおよび付随的不純物より成
る合金組成を有シフ、エレクトロスラ消溶解により得た
鋼塊を鍛造成形してタービンロータ素体としたのち、
１０９５°０以上〜１１５０°０以下の温度範囲に加
熱後焼入し、次いで５３０〜７３０’Ｃ！の温度範囲で
焼戻し処理を行なうことを特徴とするタービンロータの
製造方法。 （２、特許請求の範囲第１項において、 Ｎｂ、Ｔａの
少なくとも一種を重量慢で０，１３〜０．３％とした事
を特徴トするタービンロータの製造方法。(1) CO, 1 to 0.25 Chi, Si0 in M lid percentage
．． 5 or less, Mn 0.1-1.0%, NiO, 1
~1.0%, Cr 9.0~13.0%bMo
O, 5-2.0%, VO, 1-0.3%, N
b, at least one kind of Ta 0.03-0.3%, NO
, 03 to 0.1%, with an alloy composition consisting of Fe and incidental impurities, and a steel ingot obtained by electroslave melting was forged to form a turbine rotor body.
After heating to a temperature range of 1095°0 to 1150°0, quenching is performed, and then 530 to 730'C! A method for manufacturing a turbine rotor, characterized in that a tempering treatment is performed in a temperature range of . (2. A method for manufacturing a turbine rotor according to claim 1, characterized in that at least one of Nb and Ta is contained in an amount of 0.13 to 0.3% by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58053784A JPS59179719A (en) | 1983-03-31 | 1983-03-31 | Manufacture of turbine rotor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58053784A JPS59179719A (en) | 1983-03-31 | 1983-03-31 | Manufacture of turbine rotor |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS59179719A true JPS59179719A (en) | 1984-10-12 |
| JPS6334207B2 JPS6334207B2 (en) | 1988-07-08 |
Family
ID=12952436
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58053784A Granted JPS59179719A (en) | 1983-03-31 | 1983-03-31 | Manufacture of turbine rotor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS59179719A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6196062A (en) * | 1984-10-17 | 1986-05-14 | Mitsubishi Heavy Ind Ltd | High-chromium cast steel for high temperature service pressure vessel |
| JPS62222027A (en) * | 1986-03-25 | 1987-09-30 | Nippon Chiyuutankou Kk | Manufacture of heat resisting rotor |
| JP2006336059A (en) * | 2005-05-31 | 2006-12-14 | Toshiba Corp | Heat-resistant steel member and manufacturing method therefor |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0651319U (en) * | 1992-12-24 | 1994-07-12 | エヌティエヌ株式会社 | Soundproof metal fittings for curtain wall |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS51126917A (en) * | 1975-04-30 | 1976-11-05 | Hitachi Ltd | Process for heat treatment of 12%cr steel axle material |
| JPS5558330A (en) * | 1978-10-20 | 1980-05-01 | Toshiba Corp | Heat treating method of steam turbine rotor shaft |
| JPS56116858A (en) * | 1980-02-20 | 1981-09-12 | Toshiba Corp | Steam turbine rotor |
-
1983
- 1983-03-31 JP JP58053784A patent/JPS59179719A/en active Granted
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS51126917A (en) * | 1975-04-30 | 1976-11-05 | Hitachi Ltd | Process for heat treatment of 12%cr steel axle material |
| JPS5558330A (en) * | 1978-10-20 | 1980-05-01 | Toshiba Corp | Heat treating method of steam turbine rotor shaft |
| JPS56116858A (en) * | 1980-02-20 | 1981-09-12 | Toshiba Corp | Steam turbine rotor |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6196062A (en) * | 1984-10-17 | 1986-05-14 | Mitsubishi Heavy Ind Ltd | High-chromium cast steel for high temperature service pressure vessel |
| JPS62222027A (en) * | 1986-03-25 | 1987-09-30 | Nippon Chiyuutankou Kk | Manufacture of heat resisting rotor |
| JPH05450B2 (en) * | 1986-03-25 | 1993-01-06 | Nippon Chutanko Kk | |
| JP2006336059A (en) * | 2005-05-31 | 2006-12-14 | Toshiba Corp | Heat-resistant steel member and manufacturing method therefor |
| JP4602163B2 (en) * | 2005-05-31 | 2010-12-22 | 株式会社東芝 | Heat-resistant steel member and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6334207B2 (en) | 1988-07-08 |
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