JPS63121622A - Production of turbine rotor - Google Patents
Production of turbine rotorInfo
- Publication number
- JPS63121622A JPS63121622A JP15793687A JP15793687A JPS63121622A JP S63121622 A JPS63121622 A JP S63121622A JP 15793687 A JP15793687 A JP 15793687A JP 15793687 A JP15793687 A JP 15793687A JP S63121622 A JPS63121622 A JP S63121622A
- Authority
- JP
- Japan
- Prior art keywords
- turbine rotor
- rotor
- forging
- iron
- 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
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 25
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 20
- 239000000956 alloy Substances 0.000 claims abstract description 20
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 12
- 229910052742 iron Inorganic materials 0.000 claims abstract description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 8
- 238000005242 forging Methods 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 7
- 238000005266 casting Methods 0.000 claims abstract description 6
- 238000002844 melting Methods 0.000 claims abstract description 6
- 230000008018 melting Effects 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 238000001816 cooling Methods 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 238000005496 tempering Methods 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 239000002994 raw material Substances 0.000 claims abstract description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 10
- 239000011651 chromium Substances 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 8
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 7
- 239000010955 niobium Substances 0.000 claims description 7
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 5
- 239000011733 molybdenum Substances 0.000 claims description 5
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 5
- 239000010703 silicon Substances 0.000 claims description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 4
- 239000011572 manganese Substances 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 4
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 4
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 3
- 239000010937 tungsten Substances 0.000 claims description 3
- 229910001566 austenite Inorganic materials 0.000 abstract description 5
- 239000000155 melt Substances 0.000 abstract 2
- 238000011282 treatment Methods 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 7
- 229910000859 α-Fe Inorganic materials 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 238000004088 simulation Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 238000005452 bending Methods 0.000 description 1
- 229910021386 carbon form Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000010485 coping Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
［発明の目的］
（産業上の利用分野）
本発明はタービンロータの製造方法に係り、特に高温で
優れたクリープ強さを有するとともに、低温においても
優れた靭性ををするタービンロータの製造方法に関する
。[Detailed Description of the Invention] [Object of the Invention] (Industrial Application Field) The present invention relates to a method for manufacturing a turbine rotor, which has particularly excellent creep strength at high temperatures and excellent toughness at low temperatures. The present invention relates to a method for manufacturing a turbine rotor.
（従来の技術）
近年、」１記タービンは大容量化による熱効率の向上お
よび単位出力当たりの建設費の低減を目的として、年々
大形化し、また電力需要に応じて出力増減や起動停止と
いう機能が要求される中間負ｃｊ的運用もなされている
。このタービンの大容量化などに伴ないタービンの使用
温度は上昇し、現在蒸気タービンの最高蒸気温度は５５
６℃となり、また軸受はスパンの長い複流型中圧ロータ
や高中圧一体型ロータの採用に伴ない高温で優れたクリ
−ブ強さを有する耐熱鋼の開発が一層要求されてきてい
る。また前述したようにタービンの大吉、ｆｆｉ化に伴
ない一方ではロータ径が増加するとともにロータに埋め
込まれる動翼が長大化するのに加えてタービン起動停止
の頻繁化により起動時にタービンロータ中心部での低温
の靭性も優れたものが要求されている。(Prior art) In recent years, turbines described in item 1 have become larger year by year with the aim of increasing thermal efficiency by increasing capacity and reducing construction costs per unit output. There is also an intermediate negative cj operation that requires . As the capacity of the turbine increases, the operating temperature of the turbine increases, and currently the maximum steam temperature of a steam turbine is 55%.
6°C, and with the adoption of long-span double-flow medium-pressure rotors and high-medium pressure integrated rotors, there is an increasing demand for the development of heat-resistant steels that have excellent cleaving strength at high temperatures. In addition, as mentioned above, with the shift to FFI turbines, the rotor diameter has increased and the rotor blades embedded in the rotor have become longer. Excellent low-temperature toughness is also required.
ところで従来の蒸気タービン用の耐熱鋼としては一般ニ
Ｉ％Ｃｒ−１％Ｍｏ−０，２５％Ｖｍと称セラレル材料
や、１２％Ｃｒ系鋼で構成されている。添付図は中圧タ
ービンの構成例を示す一部切欠断面図であるが、蒸気人
口（１）の蒸気温度は５６６℃と高温化しており、かつ
ｃｒ−Ｎｏ−Ｖ 鋼或いは１２％Ｃ「系鋼で構成されて
いる従来のロータを使用した場合には、ロータ軸受はス
パン（３）から（４）の間隔が長大化しているため、動
作時には高温強度の不足からロータ曲がりが発生する。By the way, conventional heat-resistant steels for steam turbines are generally made of Cerarel material called 2%Cr-1%Mo-0.25%Vm or 12%Cr-based steel. The attached figure is a partially cutaway sectional view showing an example of the configuration of an intermediate pressure turbine, and the steam temperature of steam population (1) is as high as 566°C, and it is made of cr-No-V steel or 12% C When a conventional rotor made of steel is used, the rotor bearing has a long spacing between spans (3) and (4), which causes rotor bending during operation due to lack of high-temperature strength.
このためロータ表層（５）を冷却しているのが現状マあ
るがこれはタービン性能の低下およびタービンを複雑化
している。また高中圧−体型タービンにおいてもロータ
軸受はスパンが長くなるため高温強度のよりすぐれたー
夕が必要とされる。For this reason, the rotor surface layer (5) is currently being cooled, but this reduces turbine performance and complicates the turbine. Further, even in high-medium pressure type turbines, rotor bearings with longer spans are required to have better high-temperature strength.
さらに中間負荷的運用による起動停止の頻繁化はタービ
ンの起動時にロータ中心部（Ｇ）にかかる応力を過酷化
しつつあり、このために低温靭性にもすぐれ、脆性破壊
に対しより安全なロータが必要である。Furthermore, frequent startup and shutdown due to intermediate load operation is increasing the stress applied to the rotor center (G) when the turbine is started, which requires a rotor that has excellent low-temperature toughness and is safer against brittle fracture. It is.
なお添付図において、（２）は蒸気出口、（７）は動翼
、（８）は静翼、（９）はケーシングをそれぞれ示す。In the attached drawings, (2) indicates a steam outlet, (7) a rotor blade, (8) a stator blade, and (9) a casing, respectively.
（発明が解決しようとする問題点）
このように従来ロータでは高温のクリープ強さおよび低
温での靭性が不十分で蒸気タービンの大容量化および中
間負荷的運用には対処し得ない欠点を有している。(Problems to be Solved by the Invention) As described above, conventional rotors have insufficient creep strength at high temperatures and toughness at low temperatures, making them incapable of coping with large-capacity steam turbines and medium-load operation. are doing.
本発明は上述の問題点を考慮してなされたものであり、
高温で優れたクリープ強さを有するとともに低温での靭
性が優れたタービンロータを得ることのできる製造方法
を提供することを目的とする。The present invention has been made in consideration of the above-mentioned problems,
It is an object of the present invention to provide a manufacturing method capable of obtaining a turbine rotor having excellent creep strength at high temperatures and excellent toughness at low temperatures.
［発明の構成Ｊ
（問題点を解決するための手段および作用）本発明は、
原料合金を溶解後真空カーボン脱酸を行ない、鋳造・鍛
造の後、加熱によりオーステナイト組織に変態させ、そ
の後急冷によりマルテンサイト組織に変態させ、次いで
焼戻しを行なうことにより、化学組成が重量パーセント
でクロムｌＯ〜１３％、マンガン０．３〜１．０％、モ
リブデン０．５〜２．０％、シリコン０．２％以下、ニ
ッケル０．１〜１．５％、ニオブ０．０１〜０．５％、
バナジウム０．１〜０．５％、 ９ ングステン０．５
〜２．０％、炭素０．０５〜０．３％、窒素０．０１〜
０．１％、残部鉄および付随的不純物よりなり、実質的
に焼戻しマルテンサイト組織である鉄基合金で構成され
るタービンロータを得ることを特徴とするタービンロー
タの製造方法である。[Structure of the invention J (Means and effects for solving the problems) The present invention includes:
After melting the raw material alloy, vacuum carbon deoxidation is performed, and after casting and forging, it is transformed into an austenitic structure by heating, then transformed into a martensitic structure by rapid cooling, and then tempered, so that the chemical composition becomes chromium in weight percent. lO~13%, manganese 0.3~1.0%, molybdenum 0.5~2.0%, silicon 0.2% or less, nickel 0.1~1.5%, niobium 0.01~0.5 %,
Vanadium 0.1-0.5%, 9 ngsten 0.5
~2.0%, carbon 0.05~0.3%, nitrogen 0.01~
A method for manufacturing a turbine rotor, characterized in that the turbine rotor is made of an iron-based alloy having a substantially tempered martensitic structure, with the remainder being iron and incidental impurities.
上述の製造方法で得た特定の組成・組織の鉄基合金で構
成されるタービンロータは、高温での優れたクリープ強
さと、低温での優れた靭性を有するものとなる。A turbine rotor made of an iron-based alloy with a specific composition and structure obtained by the above manufacturing method has excellent creep strength at high temperatures and excellent toughness at low temperatures.
なお、本発明にかかる鉄基合金の化学組成は次りロム当
ニー４０ Ｘ ０％ −３０Ｘ Ｎ％−２Ｘ ＭｎＸ−
４Ｘ Ｎｊ％＋Ｃｒ％＋ 、４ｘ Ｎｏ％＋ ＯＸ Ｓ
１％＋ｌｌＸ Ｖ％＋５Ｘ Ｎｂ％＋ １．５Ｘ Ｗ％
においてクロム当量を１１以下とすることが望ましい。The chemical composition of the iron-based alloy according to the present invention is as follows:
4X Nj%+Cr%+, 4x No%+OX S
1%+llX V%+5X Nb%+1.5X W%
It is desirable that the chromium equivalent is 11 or less.
その理由としては本発明にかかる蒸気タービンロータの
ごとき大型鋼塊においてはクロム当量が１１を越えると
局部的な合金成分のばらつきからフェライト組織が生成
し、クリープ強さの低下をきたす傾向が認められるから
である。The reason for this is that in large steel ingots such as the steam turbine rotor according to the present invention, when the chromium equivalent exceeds 11, a ferrite structure is generated due to local variations in alloy composition, which tends to reduce creep strength. It is from.
本発明の製造方法を詳細に説明する。The manufacturing method of the present invention will be explained in detail.
まず所要量の元素を配合し溶解後、真空カーボン脱酸を
行なった後鋳造し、次いで例えば１１ｏＯ〜１３００℃
に加熱後さらに鍛造しロータの所定の形状にしてから、
例えば１０００〜１１５０℃の温度で完全にオーステナ
イト組織に変態するのに十分な時間熱処理を行なう。か
くして合金組織を完全にオーステナイト組織に変態させ
た後、油中或いは水噴霧等で１００℃程度まで急冷する
。この急冷により合金はγ−α−変態により実質的に均
一なマルテンサイト組織となる。しかるのち、このまま
１００℃付近に数十時間維持し均質化する。First, the required amount of elements are mixed, melted, vacuum carbon deoxidized, and then cast, for example at 11oO~1300℃.
After heating, it is further forged to the desired shape of the rotor, and then
For example, heat treatment is performed at a temperature of 1000 to 1150°C for a time sufficient to completely transform into an austenite structure. After the alloy structure is completely transformed into an austenite structure in this way, it is rapidly cooled to about 100° C. in oil or water spray. By this rapid cooling, the alloy becomes a substantially uniform martensitic structure due to γ-α transformation. Thereafter, the mixture is maintained at around 100° C. for several tens of hours to homogenize it.
さらに、例えば５００〜７００℃で数時間から数十時間
維持して焼戻しを行なうと合金組織は最終的に焼戻しマ
ルテンサイト組織となり、高温での優れたクリープ強さ
と低温での優れた靭性を有するタービンロータを得るこ
とができる。Furthermore, if tempering is carried out by maintaining the temperature at 500 to 700°C for several hours to several tens of hours, the alloy structure will eventually become a tempered martensitic structure, resulting in a turbine with excellent creep strength at high temperatures and excellent toughness at low temperatures. You can get the rotor.
ここで本発明にかかる鉄基合金の組成の限定理由を説明
する。Here, the reasons for limiting the composition of the iron-based alloy according to the present invention will be explained.
（１）クロム １０〜１３％；クロムは鉄中に固溶し合
金の強度を向上させるとともに耐酸化性、耐食性を向」
ニさせるのに必要な元素で、１０％未満では十分な強度
や耐酸化性、耐食性を得ることはできず、また１３％を
越えると好ましくないフェライト組織を生成し高温のク
リープ強さを低下させる。実用上は１０〜１１．５％、
さらには１１％未満とすることが好ましい。(1) Chromium 10-13%; Chromium dissolves in iron and improves the strength of the alloy, as well as oxidation and corrosion resistance.
If it is less than 10%, sufficient strength, oxidation resistance, and corrosion resistance cannot be obtained, and if it exceeds 13%, an undesirable ferrite structure will be formed and the high temperature creep strength will be reduced. . Practically 10-11.5%,
Furthermore, it is preferably less than 11%.
（２）マンガン ０．３〜１．０％：マンガンは溶解時
の脱酸、脱硫剤として必要な元素であり、また合金のオ
ーステナイト相の範囲を拡げる元素で、少なくとも０．
３％は必要であり、１．０％を越えると高温のクリープ
強さを低下させる。さらに実用上は０．４〜０．７％と
することが好ましい。(2) Manganese 0.3 to 1.0%: Manganese is an element necessary as a deoxidizing and desulfurizing agent during melting, and also an element that expands the range of the austenite phase of the alloy.
3% is necessary, and if it exceeds 1.0%, the high temperature creep strength will decrease. Further, in practical terms, the content is preferably 0.4 to 0.7%.
（３）モリブデン ０．５〜２．０％；モリブデンは合
金中に固溶体強化により低温および高温での強さを向上
させるとともに焼戻し脆性を防ぐのに必要な元素で０．
５％未満ではその効果が少なく、また２、０％を越える
と好ましくないフェライト相を生じ低温および高温強度
を低下させる。さらに実用上は０．８〜１．５％とする
ことが好ましい。(3) Molybdenum 0.5-2.0%; Molybdenum is an element necessary for improving the strength at low and high temperatures through solid solution strengthening in the alloy and preventing temper brittleness.
If it is less than 5%, the effect will be small, and if it exceeds 2.0%, an undesirable ferrite phase will be produced and the low and high temperature strength will be reduced. Further, in practical terms, the content is preferably 0.8 to 1.5%.
（４）シリコン ０゜２％以下；シリコンはマンガンと
同様に溶解時の脱酸剤として必要な元素であるが多量の
含有は低温での靭性を害するためなるべく少ないほうが
望ましく０．２％までとする。(4) Silicon 0°2% or less; Silicon, like manganese, is an element necessary as a deoxidizing agent during melting, but since a large amount of silicon impairs the toughness at low temperatures, it is desirable to keep it as low as possible, up to 0.2%. do.
０．２％以下という少量のＳ１含宵によりタービンロー
タのごとき大型鍛造品での偏析が防止され、均質で靭性
に優れたタービンロータを得ることができる。By containing a small amount of S1 of 0.2% or less, segregation in large forged products such as turbine rotors can be prevented, and turbine rotors that are homogeneous and have excellent toughness can be obtained.
（５）ニッケル ０．１〜１．５％；ニッケルは本発明
にかかる鉄基合金を高温でオーステナイト化組織とする
のに必要な元素で、ニッケルが存在しない場合は好まし
くないフェライト相が生成し易くなるので、これを防止
するためには少なくとも０．．１％は必要であり、１．
５％を越えると高温での強さが低下する。さらに実用上
は０．４〜１６２％とすることが好ましい。(5) Nickel 0.1-1.5%; Nickel is an element necessary to form an austenitized structure in the iron-based alloy according to the present invention at high temperatures, and in the absence of nickel, an undesirable ferrite phase will form. To prevent this, at least 0. ．． 1% is necessary and 1.
If it exceeds 5%, the strength at high temperatures will decrease. Further, in practical terms, it is preferably 0.4 to 162%.
（６）ニオブ ０．０１〜０−５９６ ；ニオブは合金
中の炭素および窒素と化合してＮｂ（ＣＮ）を生成し合
金の素地中に微細に析出分散し高温のクリープ強さを向
上させるとともに、鍛造時および熱処理時の結晶粒の粗
大化を防止し低温での靭性を向上させるのに必要な元素
で、少なくとも０．０１％は必要である。(6) Niobium 0.01 to 0-596; Niobium combines with carbon and nitrogen in the alloy to form Nb (CN), which is finely precipitated and dispersed in the matrix of the alloy, improving the creep strength at high temperatures. , is an element necessary to prevent coarsening of crystal grains during forging and heat treatment and to improve toughness at low temperatures, and is necessary in an amount of at least 0.01%.
しかし一方ではフェライト相の生成を促進させ高温のク
リープ強さを低下させるとともに過量の炭窒化物を生成
して靭性の低下をきたすので０．５％までとした。さら
に実用上は０．０４〜０．１％とすることが好ましい。However, on the other hand, it promotes the formation of ferrite phase, lowers the creep strength at high temperatures, and also generates an excessive amount of carbonitrides, resulting in a decrease in toughness, so it is limited to 0.5%. Further, in practical terms, it is preferably 0.04 to 0.1%.
（７）バナジウム ０．１〜０．５％；バナジウムは高
温のクリープ強さを向上させるために必要な元素で０．
１％未満ではその効果が十分ではなく、また０、５％を
越えるとフェライトが生成して高温のクリープ強さが低
下する。さらに実用上は０．１８〜０．２５％とするこ
とが好ましい。(7) Vanadium 0.1-0.5%; Vanadium is an element necessary to improve high-temperature creep strength.
If it is less than 1%, the effect will not be sufficient, and if it exceeds 0.5%, ferrite will be produced and the high temperature creep strength will be reduced. Further, in practical terms, it is preferably 0.18 to 0.25%.
（８）タングステン ０．５〜２．０％；タングステン
はモリブデンと同様に固溶体強化により低温および高温
での強度を向上させる元素で０．５％未満ではその効果
が顕著ではなく、また２、０％を越えると靭性を低下さ
せるのでこの範囲とする。さらに実用上は０．７〜１．
６％とすることが好ましい。(8) Tungsten 0.5-2.0%; Like molybdenum, tungsten is an element that improves strength at low and high temperatures through solid solution strengthening, and if it is less than 0.5%, the effect is not significant; If it exceeds %, the toughness decreases, so it is set within this range. Furthermore, in practical terms, it is 0.7 to 1.
It is preferably 6%.
（９）炭素 ０．０５〜０．３％；炭素は高温で鉄中に
固溶してオーステナイト組織を作り、急冷によりγ−α
′変態を起こさせ低温および高温での強さを向上させる
とともにニオブやクロムなどの元素と炭化物を形成して
高温のクリープつよさを向上させるのに必要なもので、
０．０５％未満ではその効果が小さく、また０、３％を
越えると低温での靭性が低下する。さらに実用上は０．
１１〜０．１７％とすることが好ましい。(9) Carbon 0.05-0.3%; Carbon forms a solid solution in iron at high temperatures to form an austenitic structure, and when rapidly cooled, γ-α
'It is necessary to cause transformation to improve strength at low and high temperatures, and to form carbides with elements such as niobium and chromium to improve creep strength at high temperatures.
If it is less than 0.05%, the effect will be small, and if it exceeds 0.3%, the toughness at low temperatures will decrease. Furthermore, in practice it is 0.
It is preferable to set it as 11-0.17%.
（ｌＯ）窒素 ｏ、ｏｉ〜０．１％；窒素はオーステナ
イト生成元素で焼入時のオーステナイト相を安定にし好
ましくないフェライト相の生成を抑制するとともに、他
の元素と化合して窒化物や炭窒化物を形成して高温のク
リープ強さを向上させるのに６要な元素で、０．０１％
未満ではその効果が充分でなく、また０、１％を越える
と巣やミクロポアの発生を増加させるのでこの範囲とす
る。さらに実用上は０゜０４〜０．０８％とすることが
好ましい。(lO) Nitrogen o, oi ~ 0.1%; Nitrogen is an austenite-forming element that stabilizes the austenite phase during quenching and suppresses the formation of undesirable ferrite phases, and also combines with other elements to form nitrides and carbons. Six elements necessary to form nitrides and improve high-temperature creep strength, 0.01%
If it is less than 0.1%, the effect will not be sufficient, and if it exceeds 0.1%, the occurrence of nests and micropores will increase, so this range is set. Further, in practical terms, it is preferably 0.04 to 0.08%.
（実施例） 次に本発明について実施例をもって詳細に説明する。(Example) Next, the present invention will be explained in detail using examples.
高周波真空溶解炉を用いて表−１に示す化学組成のロー
タモデル素体を溶解、鋳造した。なお真空カーボン脱酸
は鋳造前に実施した。A rotor model body having the chemical composition shown in Table 1 was melted and cast using a high frequency vacuum melting furnace. Note that vacuum carbon deoxidation was performed before casting.
次に鋳造したロータ素体を１２００℃に加熱し鍛造しロ
ータ形状化した後、各試験素材を切り出し調質熱処理を
施した。表−２に熱処理条件を示す。Next, the cast rotor body was heated to 1200° C. and forged to form a rotor shape, and then each test material was cut out and subjected to tempering heat treatment. Table 2 shows the heat treatment conditions.
なお表中のＡおよびＣはロータ材の表層部をシミュレー
トしたものであり、またＢ、Ｄは同じく中心部をシミュ
レートしたものである。Note that A and C in the table are simulations of the surface layer portion of the rotor material, and B and D are simulations of the center portion.
次にこれら準備した各合金試料から引張試験片、衝撃試
験片およびクリープ破断試験片を作製し、それぞれ試験
を行なった。これらのｖ、論結果を表−３に示す。なお
表−３の中に示した５０％ＦＡＴＴとは衝撃試験した後
試験破面において延性破面が５０％をしめる温度のこと
でこの温度が低いほど靭性が優れており、蒸気タービン
ロータとして好ましいと言える。Next, tensile test pieces, impact test pieces, and creep rupture test pieces were prepared from each of the prepared alloy samples, and tests were conducted on each of them. These results are shown in Table 3. The 50% FATT shown in Table 3 is the temperature at which 50% of the test fracture surface is ductile after an impact test.The lower this temperature is, the better the toughness is, which is preferable for steam turbine rotors. I can say that.
表−３より明らかなように、本発明のタービンロータは
従来使用されている１１ｃｒ−ＩＭｏ−０，２５Ｖロー
タ（比較例２）および比較例３，４に比ベクリープ破断
強さおよび靭性ははるかに優れ、特に比較例１のものに
比べても靭性ははるかに優れている。As is clear from Table 3, the turbine rotor of the present invention has much higher creep rupture strength and toughness than the conventionally used 11cr-IMo-0.25V rotor (Comparative Example 2) and Comparative Examples 3 and 4. The toughness is excellent, especially compared to that of Comparative Example 1.
［発明の効果］
以上説明したように本発明によれば高温のクリープ強さ
に優れ、かつ低温での靭性にも優れたタービンロータを
得ることができ、工業上すこぶる有効であるといえる。[Effects of the Invention] As explained above, according to the present invention, it is possible to obtain a turbine rotor that has excellent creep strength at high temperatures and excellent toughness at low temperatures, and can be said to be extremely effective industrially.
図は本発明を説明するための火力蒸気タービン中圧部の
構成例を示す一部切欠断面図である。
代理人弁理士 則近フＬｆ、 （Ｊｊ
同 松出光之The figure is a partially cutaway sectional view showing a configuration example of a thermal steam turbine intermediate pressure section for explaining the present invention. Representative patent attorney Norichika Lf, (Jj same Mitsuyuki Matsude)
Claims (3)
造・鍛造の後、加熱によりオーステナイト組織に変態さ
せ、その後急冷によりマルテンサイト組織に変態させ、
次いで焼戻しを行なうことにより、化学組成が重量パー
セントでクロム１０〜１３％、マンガン０．３〜１．０
％、モリブデン０．５〜２．０％、シリコン０．２％以
下、ニッケル０．１〜１．５％、ニオブ０．０１〜０．
５％、バナジウム０．１〜０．５％、タングステン０．
５〜２．０％、炭素０．０５〜０．３％、窒素０．０１
〜０．１％、残部鉄および付随的不純物よりなり、実質
的に焼戻しマルテンサイト組織である鉄基合金で構成さ
れるタービンロータを得ることを特徴とするタービンロ
ータの製造方法。(1) After melting the raw material alloy, vacuum carbon deoxidation is performed, and after casting and forging, it is transformed into an austenitic structure by heating, and then transformed into a martensitic structure by rapid cooling,
Then, by tempering, the chemical composition becomes 10 to 13% chromium and 0.3 to 1.0% manganese in weight percent.
%, molybdenum 0.5-2.0%, silicon 0.2% or less, nickel 0.1-1.5%, niobium 0.01-0.
5%, vanadium 0.1-0.5%, tungsten 0.
5-2.0%, carbon 0.05-0.3%, nitrogen 0.01
1. A method for manufacturing a turbine rotor, comprising obtaining a turbine rotor composed of an iron-based alloy having a substantially tempered martensitic structure, the balance being iron and incidental impurities.
０℃であることを特徴とする特許請求の範囲第１項記載
のタービンロータの製造方法。(2) Heating temperature for austenitization is 1000-115
The method for manufacturing a turbine rotor according to claim 1, wherein the temperature is 0°C.
徴とする特許請求の範囲第１項記載のタービンロータの
製造方法。(3) The method for manufacturing a turbine rotor according to claim 1, wherein the tempering temperature is 550 to 700°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15793687A JPS63121622A (en) | 1987-06-26 | 1987-06-26 | Production of turbine rotor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15793687A JPS63121622A (en) | 1987-06-26 | 1987-06-26 | Production of turbine rotor |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP55019201A Division JPS6054385B2 (en) | 1980-02-20 | 1980-02-20 | heat resistant steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63121622A true JPS63121622A (en) | 1988-05-25 |
| JPH0333765B2 JPH0333765B2 (en) | 1991-05-20 |
Family
ID=15660717
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15793687A Granted JPS63121622A (en) | 1987-06-26 | 1987-06-26 | Production of turbine rotor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63121622A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112680663A (en) * | 2020-12-11 | 2021-04-20 | 钢铁研究总院 | 9% Ni steel oversized rotor forging for ultralow temperature engineering and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3767390A (en) * | 1972-02-01 | 1973-10-23 | Allegheny Ludlum Ind Inc | Martensitic stainless steel for high temperature applications |
-
1987
- 1987-06-26 JP JP15793687A patent/JPS63121622A/en active Granted
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3767390A (en) * | 1972-02-01 | 1973-10-23 | Allegheny Ludlum Ind Inc | Martensitic stainless steel for high temperature applications |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112680663A (en) * | 2020-12-11 | 2021-04-20 | 钢铁研究总院 | 9% Ni steel oversized rotor forging for ultralow temperature engineering and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0333765B2 (en) | 1991-05-20 |
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