JP2007002679A - High/low pressure-integrated steam turbine rotor and its manufacturing method, and high/low pressure-integrated steam turbine and its manufacturing method - Google Patents
High/low pressure-integrated steam turbine rotor and its manufacturing method, and high/low pressure-integrated steam turbine and its manufacturing method Download PDFInfo
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本発明は、新規な高低圧一体型タービンロータとその製造法及び高低圧一体型蒸気タービンとその製造法に関する。 The present invention relates to a novel high-low pressure integrated turbine rotor and a manufacturing method thereof, and a high-low pressure integrated steam turbine and a manufacturing method thereof.
発電機のタービンの1つとして、高圧部から低圧部までを一体化した高低圧一体型タービンが知られており、このタービンには高低圧一体烈タービンロータが用いられている。このタービンロータは、高温で高圧から低圧に至る蒸気圧力にさらされており、その材料には、優れた高温クリープ特性と、優れた低温靭性とを兼ね備えていることが要求される。 As one of the turbines of a generator, a high-low pressure integrated turbine in which a high-pressure part to a low-pressure part are integrated is known, and a high-low pressure integrated turbine rotor is used for this turbine. This turbine rotor is exposed to steam pressure from high pressure to low pressure at high temperatures, and the material is required to have excellent high temperature creep characteristics and excellent low temperature toughness.
従来、高低圧一体型タービンロータ材としては、Cr−Mo−V系低合金鋼が開発されており、例えば特許文献1には、この種の材料を改良した低合金鋼を用いた高低圧一体型タービンロータの製造方法が開示されている。ところが、最近では、より大容量および高効率化を指向した発電プラントが開発され、蒸気タービンの高効率化技術として低圧最終設動翼の長尺化が進んでいる。
Conventionally, Cr—Mo—V-based low alloy steel has been developed as a high-low pressure integrated turbine rotor material. For example,
しかしながら、低圧最終」裂動翼の長尺化に伴い、タービンロータの低圧最終設に相当する部分の引張強さや低温靭性を改善必要がある。しかし、高温クリープ特性を保ちながら、引張強さおよび低温靭性を向上させることは、従来の同一材質の高低圧一体型タービンロータでは、この要求に応えることが困難である。これを解決する手段として、タービンロータ各部の組成を変えることにより、各部の必要特性を満足させることが考えられ、例えば特許文献2には、異なる組成を有する2個以上のロータ部分素材を結合して一体とした高低圧一体型タービンロータが開示されている。
However, with the increase in the length of the low pressure final cracking blade, it is necessary to improve the tensile strength and low temperature toughness of the portion corresponding to the low pressure final installation of the turbine rotor. However, improving the tensile strength and low temperature toughness while maintaining high temperature creep characteristics is difficult to meet this requirement with conventional high and low pressure integrated turbine rotors of the same material. As a means for solving this, it is conceivable to satisfy the required characteristics of each part by changing the composition of each part of the turbine rotor. For example, in
上述したタービンロータは、各部の特性を満たす一体型タービンロータを構成することが可能であるが、異なる組成のロータ部分素材を複数製造することが必要である。そのため、上述した方法により、低圧最終設部の引張強さ低温靭性を向上させた、一体型タービンロータを製造するには、多くの製造工程、時間、コストがかかる。 The above-described turbine rotor can constitute an integrated turbine rotor that satisfies the characteristics of each part, but it is necessary to manufacture a plurality of rotor partial materials having different compositions. Therefore, it takes many manufacturing steps, time, and costs to manufacture an integrated turbine rotor in which the tensile strength and low temperature toughness of the low-pressure final installation portion are improved by the above-described method.
また、結合部が存在するため、結合箇所と手法を選定しなければ、同一材質の高低圧一体型タービンロータよりも信頼性で不安を残す。近年の火カプラントでは、効率向上だけでなく優れた経済性も要求され、タービン材料においても従来同等あるいはそれ以上の機械的性質や製造性を確保しながら、経済性に優れることが不可欠である。 In addition, since there is a coupling portion, if the coupling location and method are not selected, there remains anxiety with reliability more than the high- and low-pressure integrated turbine rotor made of the same material. Recent fire power plants are required not only to improve efficiency but also to have excellent economic efficiency, and it is indispensable for turbine materials to be excellent in economic efficiency while securing mechanical properties and manufacturability equivalent to or higher than those of conventional turbine materials.
本発明の目的は、高圧部において優れた高温クリープ強度を有し、又、低圧最終設部において優れた引張強度と低温靱性を有し、低圧最終段部に植設される動翼としてマルテンサイト鋼を用いた翼部長さで、3600rpm蒸気タービンでは914mm(36")以上、3600rpm蒸気タービンでは1092mm(43")以上の長翼化が可能である高低圧一体型蒸気タービン用ロータシャフトとその製造法及び高低圧一体型蒸気タービンとその製造法を提供することにある。 The object of the present invention is to provide martensite as a moving blade to be implanted in the low-pressure final stage portion, having excellent high-temperature creep strength in the high-pressure portion, and having excellent tensile strength and low-temperature toughness in the low-pressure final portion. Rotor shaft for high- and low-pressure integrated steam turbines with blade lengths using steel, which can be longer than 914 mm (36 ") for a 3600 rpm steam turbine and longer than 1092 mm (43") for a 3600 rpm steam turbine, and its manufacture And to provide a high and low pressure integrated steam turbine and a method of manufacturing the same.
本発明は、C、Si、Mn、Ni、Cr、Mo及びVを含有するベーナイト組織を有する耐熱鋼からなる高圧側部分と、C、Si、Mn、Ni、Cr、Mo及びVを含有前記高圧側のNi量より多いNi量を有するベーナイト組織を有する耐熱鋼からなる低圧最終設部とを有し、該低圧最終段部のC、Si、Mn、Cr、Mo及びVの含有量は前記高圧側部分のそれらと同等又は前記Ni量の増化に従ってやや減少していることを特徴とする高低圧一体型蒸気タービン用ロータシャフトにある。 The present invention includes a high-pressure side portion made of a heat-resistant steel having a bainite structure containing C, Si, Mn, Ni, Cr, Mo and V, and the high pressure containing C, Si, Mn, Ni, Cr, Mo and V. Low-pressure final part made of heat-resistant steel having a bainite structure with a Ni content greater than the Ni content on the side, and the content of C, Si, Mn, Cr, Mo and V in the low-pressure final stage part is the high pressure The rotor shaft for a high and low pressure integrated steam turbine is characterized in that it is the same as those in the side portion or slightly decreased as the amount of Ni increases.
前記高圧側部分は、重量で、C0.15〜0.40%、Si0.20%以下、Mn0.05〜0.80%、Ni0.5〜2.5%、Cr0.8〜2.5%、Mo0.3〜2.5%、V0.07〜0.35%を含有する耐熱鋼からなり、前記低圧最終設部は、重量で、C0.15〜0.40%、Si0.20%以下、Mn0.05〜0.80%、Ni3.25〜4.10%、Cr0.8〜2.5%、Mo0.3〜2.5%、V0.07〜0.35%を耐熱鋼からなり、該低圧最終段部のC、Si、Mn、Cr、Mo及びVの含有量が前記高圧側部分のNi量に対して増化するNi量の割合に従って減少していることを特徴とする。 The high-pressure side portion is C0.15 to 0.40%, Si 0.20% or less, Mn 0.05 to 0.80%, Ni 0.5 to 2.5%, Cr 0.8 to 2.5% by weight. , Mo 0.3-2.5%, V0.07-0.35% containing heat resistant steel, the low-pressure final installation part is C0.15-0.40% by weight, Si 0.20% or less , Mn 0.05-0.80%, Ni 3.25-4.10%, Cr 0.8-2.5%, Mo 0.3-2.5%, V0.07-0.35% made of heat resistant steel The content of C, Si, Mn, Cr, Mo and V in the low-pressure last stage portion is reduced according to the ratio of the Ni amount increasing with respect to the Ni amount in the high-pressure side portion.
前記高圧側部分は、重量で、CO.20〜0.28%、Si0.02〜0.15%、Mn0.15〜0.25%、Ni1.70〜1.90%、Cr1.90〜2.10%、Mo1.10〜1.30%、V0.25〜0.30%を含有する耐熱鋼からなり、前記低圧最終段部は、重量で、C0.20〜0.28%、Si0.02〜0.15%、Mn0.15〜0.25%、Ni3.25〜4.10%、Cr1.90〜2.10%、Mo1.10〜1.30%、V0.25〜0.30%を含有する耐熱鋼からなることが好ましい。 The high pressure side portion is CO. 20 to 0.28%, Si 0.02 to 0.15%, Mn 0.15 to 0.25%, Ni 1.70 to 1.90%, Cr 1.90 to 2.10%, Mo 1.10 to 1.30 %, V0.25 to 0.30% heat-resistant steel, and the low-pressure final stage part is C0.20 to 0.28% by weight, Si 0.02 to 0.15%, Mn 0.15 to It is preferably made of a heat resistant steel containing 0.25%, Ni 3.25 to 4.10%, Cr 1.90 to 2.10%, Mo 1.10 to 1.30%, V 0.25 to 0.30%. .
前記高圧側部分と前記低圧最終設部との間に前記耐熱鋼の合金組成が徐々に変化する傾斜領域を有すること、前記傾斜領域の軸方向幅が300mm以下であること、前記高圧側部分は、高圧部及び低圧部又は高圧部、中圧部及び低圧部を有することが好ましい。 Having an inclined region where the alloy composition of the heat-resistant steel gradually changes between the high-pressure side portion and the low-pressure final portion, the axial width of the inclined region is 300 mm or less, the high-pressure side portion is It is preferable to have a high pressure part and a low pressure part or a high pressure part, an intermediate pressure part and a low pressure part.
又、本発明は、C、Si、Mn、Ni、Cr、Mo及びVを含有し熱処理によってベーナイト組織が形成される耐熱鋼の端部円周面にNi材を配置して、該Ni材を有する前記端部をNi材と共に溶解し、前記Ni量より多いNi含有量を有する耐熱鋼からなる低圧最終段部を形成し、前記Ni材の配置していない部分を高圧側部分とすることを特徴とする高低圧一体型蒸気タービン用ロータシャフトの製造法にある。 The present invention also includes a Ni material disposed on the circumferential surface of the end portion of the heat-resistant steel containing C, Si, Mn, Ni, Cr, Mo and V and forming a bainite structure by heat treatment. Melting the end portion together with the Ni material, forming a low-pressure final step portion made of heat-resistant steel having a Ni content greater than the Ni content, and making the portion where the Ni material is not disposed a high-pressure side portion It is in the manufacturing method of the rotor shaft for high and low pressure integrated steam turbines characterized.
更に、本発明は、重量で、C0.15〜0.40%、Si0.20%以下、Mn0.05〜0.80%、Ni0.5〜2.5%、Cr0.8〜2.5%、Mo0.3〜2.5%、V0.07〜0.35%を含有する耐熱鋼の端部円周面に、Ni材を配置して、該Ni材を有する部分の前記端部をNi材と共に溶解し、重量で、C0.15〜0.40%、Si0.20%以下、Mn0.05〜0.80%、Ni3.25〜4.10%、Cr0.8〜2.5%、Mo0.3〜2.5%、V0.07〜0.35%を耐熱鋼からなる低圧最終段部を形成し、前記Ni材の配置していない部分を高圧側部分とすることを特徴とする高低圧一体型タービンロータの製造法にある。 Furthermore, the present invention, by weight, C0.15-0.40%, Si0.20% or less, Mn0.05-0.80%, Ni0.5-2.5%, Cr0.8-2.5% Ni material is disposed on the circumferential surface of the end portion of the heat-resistant steel containing Mo 0.3 to 2.5% and V 0.07 to 0.35%, and the end portion of the portion having the Ni material is Ni. It dissolves with the material, and by weight, C0.15 to 0.40%, Si 0.20% or less, Mn0.05 to 0.80%, Ni3.25 to 4.10%, Cr0.8 to 2.5%, A low-pressure final step portion made of heat-resistant steel is formed with Mo of 0.3 to 2.5% and V of 0.07 to 0.35%, and the portion where the Ni material is not arranged is a high-pressure side portion. It is in the manufacturing method of the high and low pressure integrated turbine rotor.
前記Ni材を配置した前記低圧最終設部に相当する端部より前記高圧側部分に掛けて順次前記溶解すること、前記Ni材を前記低圧最終段部のNi量に応じて前記円周面に均等に配置すること、前記Ni材がNi線であり、該Ni線を前記低圧最終段部のNi量に応じて前記円周面に均等に軸方向に配置又は巻回することが好ましい。 The melting is sequentially performed from the end corresponding to the low pressure final installation portion where the Ni material is disposed to the high pressure side portion, and the Ni material is applied to the circumferential surface according to the amount of Ni in the low pressure final stage portion. Preferably, the Ni material is a Ni wire, and the Ni wire is evenly arranged or wound in the axial direction on the circumferential surface according to the amount of Ni in the low-pressure final stage portion.
前記高圧側部分及び低圧最終段部を同一温度に加熱し、前記高圧部、又は前記高圧部と中圧部が前記低圧部及び低圧最終設部よりも遅い冷却速度で焼入れを行うこと、前記高圧部、又は前記高圧部と中圧部が前記低圧部及び低圧最終設部よりも高温で焼入れを行うこと、前記高圧部、又は前記高圧部と中圧部が前記低圧部及び低圧最終設部よりも高温で焼戻しを行うこと、更に前記溶解をエレクトロスラグ溶解によって順次行うこと、前記高圧側部分と前記低圧最終段部との間に前記耐熱鋼の合金組成が徐々に変化する傾斜領域を有し、該傾斜領域の軸方向幅が300mm以下、好ましくは200〜300mmとなるように前記溶解時の溶解量の厚さを制御することが好ましい。 Heating the high-pressure side part and the low-pressure final stage part to the same temperature, and quenching the high-pressure part or the high-pressure part and the intermediate-pressure part at a slower cooling rate than the low-pressure part and the low-pressure final installation part, Or the high pressure part and the intermediate pressure part are hardened at a higher temperature than the low pressure part and the low pressure final installation part, the high pressure part, or the high pressure part and the intermediate pressure part are from the low pressure part and the low pressure final installation part. Tempering at a high temperature, further performing the melting sequentially by electroslag melting, and having an inclined region in which the alloy composition of the heat-resistant steel gradually changes between the high-pressure side portion and the low-pressure final stage portion. It is preferable to control the thickness of the dissolution amount at the time of dissolution so that the axial width of the inclined region is 300 mm or less, preferably 200 to 300 mm.
本発明は、高圧側部分及び低圧最終段部に亘って一体に形成された動翼が植設されるロートシャフトを備え、一車室からなる高低圧一体型蒸気タービンにおいて、前記ロータシャフトが前述に記載の高低圧一体型蒸気タービン用ロータシャフトよりなり、蒸気温度として538〜593℃に適用可能である。 The present invention includes a funnel shaft in which a moving blade integrally formed over a high-pressure side portion and a low-pressure last stage portion is provided, and in the high-low pressure integrated steam turbine including a single casing, the rotor shaft is the above-mentioned. The high-low pressure integrated steam turbine rotor shaft described in 1) is applicable to a steam temperature of 538 to 593 ° C.
本発明は、高圧側部分と低圧最終段部とに亘って一体に形成され動翼が植設されるロートシャフトを製造する一車室からなる高低圧一体型蒸気タービンの製造法において、前記ロータシャフトの製造法が前述に記載の高低圧一体型蒸気タービン用ロータシャフトの製造法からなることを特徴とする。 The present invention relates to a method for producing a high-low pressure integrated steam turbine comprising a single casing for producing a funnel shaft that is integrally formed between a high-pressure side portion and a low-pressure final stage portion and in which a moving blade is implanted. The method for producing the shaft is characterized by comprising the method for producing a rotor shaft for a high-low pressure integrated steam turbine described above.
本願発明の高低圧一体型蒸気タービン用ロータシャフトは、低圧最終段部にNiを添加し(以下、組成偏差)、低圧ロータに用いられる3.5Ni−Cr−Mo−V系鋼の組成改良鋼とすることができる。 The rotor shaft for a high and low pressure integrated steam turbine according to the present invention is obtained by adding Ni (hereinafter referred to as composition deviation) to the low pressure final stage portion and improving the composition of 3.5Ni-Cr-Mo-V steel used for the low pressure rotor. It can be.
また、タービンロータ素体の高中圧部と低圧部によって焼入れ時の冷却速度を変える偏差冷却することで、高中圧部に相当する部分は十分な高温クリープ強皮が確保され、一方、低圧部では優れた低温靭性が、低圧最終段部では高い引張強さが確保される。さらに、焼入れ及び焼戻しの際に、加熱温度を高中圧部と低圧部で差異を設ける偏差加熱することで、上記作用が一層向上する。 In addition, by performing differential cooling that changes the cooling rate during quenching by the high and low pressure portions of the turbine rotor body, a portion corresponding to the high and medium pressure portions is secured with a sufficient high-temperature creep strong skin, whereas in the low pressure portion, Excellent low-temperature toughness ensures high tensile strength at the low-pressure final stage. Furthermore, the above-mentioned effect | action improves further by carrying out the deviation heating which provides a difference in a heating temperature in a high intermediate pressure part and a low pressure part in hardening and tempering.
合金組成の偏差方法は、添加するNi材としてワイヤやリング等をロータ素体に対し等間隔に取り付け、または管やネット等をロータ素体に被せるように取り付ける。いずれの方法を用いても、ロータ素体の軸の同心円状に取り付けることで、再溶解時に組成の均一化がなされやすい。 As a deviation method of the alloy composition, a wire, a ring, or the like is attached to the rotor element body at equal intervals as a Ni material to be added, or a pipe, a net, or the like is attached to the rotor element body. Regardless of which method is used, the composition is easily uniformed at the time of remelting by concentrically attaching the rotor element shaft.
ところで、Ni以外にも組成を変えたい部位に、他元素や合金を取り付け再溶解することでロータ各部の組成を変えることが可能である。また、その他の公知の耐熱鋼を採用し、その低圧最終段部および低圧部にNiを添加しても、同様に高い引張強さおよび低温靭性が確保することが可能である。さらに、複数元素を単体および合金化して、タービンロータ素体の各部位に添加することで相当部の組成を変え必要特性を得ることも可能であり、製造方法の適用範囲が広い。この組成偏差方法は、従来の電極継足しによるロータの組成変化方法に比べて、経済性に優れ、比較的簡便にロータ各部の特性を変更することが可能である。 By the way, it is possible to change the composition of each part of the rotor by attaching and remelting other elements and alloys to the part other than Ni where the composition is to be changed. Further, even when other known heat-resistant steel is employed and Ni is added to the low-pressure final stage portion and the low-pressure portion, high tensile strength and low-temperature toughness can be similarly secured. Furthermore, it is possible to change the composition of the corresponding part by obtaining a plurality of elements as a single element and alloy and adding them to each part of the turbine rotor body to obtain necessary characteristics, and the range of application of the manufacturing method is wide. This composition deviation method is more economical than the conventional method of changing the composition of the rotor by adding electrodes, and the characteristics of each part of the rotor can be changed relatively easily.
次に、低圧最終段にNiを加える理由を説明する。Niは焼入れ性を向上させ、引張強度及び靭性を向上させる。ただし、含有量が増えるとクリープ強度を低下させるため、高圧ではNi含有量を適正範囲に抑える必要がある。 Next, the reason why Ni is added to the low-pressure final stage will be described. Ni improves hardenability and improves tensile strength and toughness. However, when the content increases, the creep strength decreases, so it is necessary to keep the Ni content within an appropriate range at high pressure.
合金組成の傾斜領域は、その幅を狭くすることで傾斜領域を低圧最終段とその前設との段落間にすることができ、ダブテイル部の組成は均質に保たれる。高圧側に組成傾斜領域が入っても機械的性質には間題ないが、軸方向の傾斜領域が広がることで円周方向の組成傾斜の可能性があり、これは経年曲がりを誘発する原因にもなる。そのため円周方向の組成傾斜を抑える観点から傾斜領域を300mm以下とすることが望ましい。 By narrowing the width of the gradient region of the alloy composition, the gradient region can be made between the low-pressure final stage and its predecessor stage, and the composition of the dovetail portion is kept uniform. There is no problem with the mechanical properties even if a composition gradient region enters the high-pressure side, but there is a possibility of a composition gradient in the circumferential direction by expanding the axial gradient region, which is the cause of inducing aged bending. Also become. Therefore, it is desirable that the inclined region be 300 mm or less from the viewpoint of suppressing the composition inclination in the circumferential direction.
本発明の高低圧一体型蒸気タービンロータを構成する低合金鋼の組成及び熱処理条件について説明する。 The composition and heat treatment conditions of the low alloy steel constituting the high and low pressure integrated steam turbine rotor of the present invention will be described.
Cは、焼入性を向上し強度を確保するのに必要な元素である。その量が0.15%以下では十分な焼入性が得られず、ロータ中心に軟らかいフエライト組織が生成し、十分な引張強さ及び耐力が得られない。また0.4%以上になると靭性を低下させるので、Cの範囲はO.15〜0.4%、特にCは0.20〜0.28%の範囲が好ましい。 C is an element necessary for improving hardenability and ensuring strength. If the amount is 0.15% or less, sufficient hardenability cannot be obtained, a soft ferrite structure is formed at the center of the rotor, and sufficient tensile strength and yield strength cannot be obtained. Further, if it exceeds 0.4%, the toughness is lowered, so the range of C is O.D. 15 to 0.4%, especially C is preferably in the range of 0.20 to 0.28%.
Si及びMnは従来脱酸剤として添加していたが、真空C脱酸法及びエレクトロスラグ再溶解法などの製鋼技術によれは、特に添加しなくとも健全なロータが溶製可能である。長時間使用による脆化の点から、Si及びMnは低目にすべきであり、それぞれ0.20%以下及び0.05〜0.80%が好ましく、特にSi0.02〜0.15%、Mn0.10〜0.25%が好ましい。 Conventionally, Si and Mn have been added as deoxidizers. However, according to steelmaking techniques such as the vacuum C deoxidation method and the electroslag remelting method, a healthy rotor can be melted without particular addition. From the viewpoint of embrittlement due to long-term use, Si and Mn should be low, preferably 0.20% or less and 0.05 to 0.80%, respectively, especially Si 0.02 to 0.15%, Mn is preferably 0.10 to 0.25%.
一方、極少量のMn添加は、熱間加工性を悪くする有害なSを、硫化物MnSとして固定する作用があるために、Mnの極微量添加は、前述のSの害を減少する効果があるので、蒸気タービン用ロータシャフトのような大型鍛造品の製造においては0.10〜0.25%含有するのが好ましい。 On the other hand, the addition of a very small amount of Mn has the effect of fixing harmful S that deteriorates hot workability as sulfide MnS. Therefore, the addition of a very small amount of Mn has the effect of reducing the harm of S described above. Therefore, in the production of a large forged product such as a rotor shaft for a steam turbine, the content is preferably 0.10 to 0.25%.
Niは、本発明の高低圧一体型蒸気タービン用ロータシャフト材として最も特徴的な元素で、焼入れ性を向上させ、靭性向上に不可欠の元素である。高圧部においては0.5%未満では靭性向上効果が十分でない。また2.5%を超える多量の添加は、クリープ破断強度を低下させてしまう。特に1.6〜2.0%、より1.7〜1.9%の範囲が好ましい。又、低圧部においては、3.25%未満では靭性向上効果が十分でなく、また4.10%を超える多量の添加を行っても、より高い強度及び靭性が得られない。 Ni is the most characteristic element for the rotor shaft material for the high and low pressure integrated steam turbine of the present invention, and is an element essential for improving hardenability and improving toughness. In the high pressure part, if it is less than 0.5%, the effect of improving toughness is not sufficient. Moreover, the addition of a large amount exceeding 2.5% reduces the creep rupture strength. In particular, the range of 1.6 to 2.0%, more preferably 1.7 to 1.9% is preferable. In the low pressure portion, if the amount is less than 3.25%, the effect of improving toughness is not sufficient, and even if a large amount of addition exceeding 4.10% is added, higher strength and toughness cannot be obtained.
Crは、焼入れ性を向上させ、靭性及び強度向上効果がある。また蒸気中の耐食性も向上させる。0.8%未満ではこれらの効果が十分でなく、2.5%を超える添加は、クリープ破断強度を低下させる。特に1.7〜2.3%、より1.9〜2.1%が好ましい。 Cr improves hardenability and has an effect of improving toughness and strength. It also improves the corrosion resistance in steam. If it is less than 0.8%, these effects are not sufficient, and if it exceeds 2.5%, the creep rupture strength is lowered. In particular, 1.7 to 2.3% and more preferably 1.9 to 2.1% are preferable.
Moは、焼戻し処理中に結晶粒内に微細炭化物を析出させ、高温強度向上及び焼戻し脆化防止効果がある。しかし、0.3%未満ではこれらの効果が十分でなく、2.5%を超える多量の添加は靭性を添加させる。特に強度と靭性の点から1.0〜1.5%、より1.1〜1.3%が好ましい。 Mo precipitates fine carbides in the crystal grains during the tempering treatment, and has an effect of improving high temperature strength and preventing temper embrittlement. However, if less than 0.3%, these effects are not sufficient, and a large amount exceeding 2.5% adds toughness. In particular, from the viewpoint of strength and toughness, 1.0 to 1.5%, more preferably 1.1 to 1.3% is preferable.
Vは、焼戻し処理中に結晶粒内に微細炭化物を析出させ、高温強度及び靭性向上効果がある。0.07%未満ではこれらの効果が十分でなく、0.35%を超える添加は効果が飽和してしまう。特に0.20〜0.30%、より0.25〜0.30%の範囲が好ましい。 V precipitates fine carbides in crystal grains during the tempering treatment, and has an effect of improving high-temperature strength and toughness. If it is less than 0.07%, these effects are not sufficient, and if it exceeds 0.35%, the effect is saturated. In particular, the range of 0.20 to 0.30%, more preferably 0.25 to 0.30% is preferable.
本発明の組成からなる低合金を溶製するときに、希土類元素(La、Ce等)、Ca、Zr及びA1のいずれかを添加することにより靭性が向上する。希土類元素は0.05%未満では効果が不十分で、0.4%を超える添加はその効果が飽和する。Caは少量の添加で靭性向上効果があるが、0.0005%未満では効果が不十分で、0.01%を超える添加はその効果が飽和する。Zrは0.01%未満では靭性向上効果が不十分であり、0.2%を超える添加はその効果が飽和する。A1は0、001%未満では靭性向上効果が不十分であり、0.02%を超える添加はクリープ破断強度を低下させる。 When melting a low alloy having the composition of the present invention, toughness is improved by adding any of rare earth elements (La, Ce, etc.), Ca, Zr and A1. If the rare earth element is less than 0.05%, the effect is insufficient, and the addition exceeding 0.4% saturates the effect. Ca has an effect of improving toughness when added in a small amount, but if it is less than 0.0005%, the effect is insufficient, and if it exceeds 0.01%, the effect is saturated. If Zr is less than 0.01%, the effect of improving toughness is insufficient, and the addition exceeding 0.2% saturates the effect. If A1 is less than 0, 001%, the effect of improving toughness is insufficient, and addition exceeding 0.02% lowers the creep rupture strength.
Nb及びTaの少なくとも1種を0.005〜0.15%添加するのが好まし0.15%を超えると蒸気夕一ビン用ロータシャフトの如く大型構造物ではこれらの巨大な炭化物が晶出し強度及び靭性を低めるので0.005〜0.15%とする。特に0.02〜0.07%が好ましい。 It is preferable to add 0.005 to 0.15% of at least one of Nb and Ta, and when it exceeds 0.15%, these huge carbides crystallize in a large structure such as a rotor shaft for a steam bottle. Since strength and toughness are lowered, the content is made 0.005 to 0.15%. Especially 0.02 to 0.07% is preferable.
Wは強度を高めるため0.1%以上加えるのが好ましいが、1.0%を超えると大型鋼塊においては偏析の間題が生じる等強度を低めるので、0.1〜1.0%とするのが好ましい。好ましくは0.1〜0.5%である。 W is preferably added in an amount of 0.1% or more in order to increase the strength. However, if it exceeds 1.0%, the problem of segregation occurs in large steel ingots. It is preferable to do this. Preferably it is 0.1 to 0.5%.
本発明は、高低圧一体型蒸気夕ービン用口ータシャフトとして、その高圧部の530℃、105h平滑及び切欠クリープ破断強度が13kg/mm2以上、低圧部の引張強さが84kg/mm2以上、破面遷移温度が35℃以下とするのが好ましい。このように優れた機械的性質を得るため次の様な傾斜調質熱処理を施すのが好ましい。この調質熱処理を施す前に、金属組織を微細にするために、650度〜710℃で70時間以上保持する処理を施すのが好ましい。 The present invention is a high pressure / low pressure integrated steam evening bottle mouth shaft. The high pressure portion has a high pressure portion of 530 ° C., 10 5 h smoothness and notch creep rupture strength of 13 kg / mm 2 or more, and the low pressure portion has a tensile strength of 84 kg / mm 2. As described above, the fracture surface transition temperature is preferably 35 ° C. or lower. In order to obtain such excellent mechanical properties, the following gradient tempering heat treatment is preferably performed. Before performing this tempering heat treatment, in order to make the metal structure fine, it is preferable to perform a treatment of holding at 650 ° C. to 710 ° C. for 70 hours or more.
次に、上記組成のタービンロータ素体に施す熱処理の条件について説明する。焼入れ加熱温度として、全体を均一加熱する場合には、そのオーステナイト化温度は、900℃未満では、十分な高温クリープ強度が得られにくく、1000℃を超えると、低温靱性が低下するので、900〜1000℃が望ましい。 Next, conditions for heat treatment applied to the turbine rotor body having the above composition will be described. As the quenching heating temperature, when the whole is uniformly heated, if the austenitizing temperature is less than 900 ° C, sufficient high-temperature creep strength is difficult to obtain, and if it exceeds 1000 ° C, the low-temperature toughness decreases, so 900- 1000 ° C. is desirable.
高中圧部900〜1030℃、低圧部870〜1000℃の偏差加熱する場合には、(高中圧部温度−低圧部温度)を20〜80℃とし、高中圧部におけるオーステナイト化温度が900℃未満であると十分な高温クリープ強度が得られにくく、1030℃を超えると高温での切欠弱化が生じるおそれがあるため上記範囲とするのが望ましい。 In the case of deviation heating of the high and medium pressure part 900 to 1030 ° C. and the low pressure part 870 to 1000 ° C., the (high and medium pressure part temperature−low pressure part temperature) is set to 20 to 80 ° C. If it is, it is difficult to obtain a sufficient high-temperature creep strength, and if it exceeds 1030 ° C., there is a risk of notch weakening at a high temperature, so the above range is desirable.
一方、低圧部のオーステナイト化温度は、870℃未満では、炭化物が完全に固溶しないため低温靱性が低く、また、1000℃を超えるとオーステナイト結晶粒が粗大化して低温靱性が低下する恐れがあることから上記範囲とするのが望ましい。なお、高中圧部のオーステナイト化温度は、低圧部のオーステナイト化温度よりも20℃以上の温度差を付け、その温度差が80℃を超えると製造が難しいため、その温度差の範囲を20〜80℃にするのが好ましい。 On the other hand, if the austenitizing temperature of the low pressure part is less than 870 ° C., the carbide does not completely dissolve, so the low temperature toughness is low, and if it exceeds 1000 ° C., the austenite crystal grains become coarse and the low temperature toughness may decrease. Therefore, the above range is desirable. Note that the austenitizing temperature of the high and medium pressure part has a temperature difference of 20 ° C. or more than the austenitizing temperature of the low pressure part, and if the temperature difference exceeds 80 ° C., it is difficult to produce, so the temperature difference range is 20 to 20 ° C. It is preferable to set it at 80 ° C.
冷却速度として、高中圧部に相当する部分で良好な高温クリープ強度が得て、低圧部に相当する部分で良好な低温靭性を得るために、高中圧部の冷却速度を低圧部の冷却速度よりも遅くする。高中圧部に相当する部分を衝風冷却又は空冷の冷却速度で焼入れする望ましい。また、低圧部に相当する部分は、油冷、水冷、噴水冷却の冷却速度で焼入れするのが望ましい。 In order to obtain a good high temperature creep strength at the part corresponding to the high and medium pressure part and a good low temperature toughness at the part corresponding to the low pressure part, the cooling rate of the high and medium pressure part is changed from the cooling rate of the low pressure part. Also slow down. It is desirable to quench the portion corresponding to the high and medium pressure portion at a cooling rate of blast cooling or air cooling. Further, it is desirable to quench the portion corresponding to the low pressure portion at a cooling rate of oil cooling, water cooling, or fountain cooling.
焼戻しは、550〜700℃で行われ、その回数は、鋼の組成、必要な焼戻し効果などに従って適宜選定される。焼戻し温度が、550℃未満であると、良好な靱性を得ることができず、700℃を超えると所望の強度が得られにくい。一次焼戻しは、550〜615℃に加熱・保持後徐冷、2次焼戻しは620〜670℃に加熱・保持するのが好ましい。又、焼戻温度においても高圧側を低圧側にくらべ高い温度で焼戻しするのがよい。 Tempering is performed at 550 to 700 ° C., and the number of times is appropriately selected according to the composition of the steel, the necessary tempering effect, and the like. When the tempering temperature is less than 550 ° C., good toughness cannot be obtained, and when it exceeds 700 ° C., it is difficult to obtain a desired strength. It is preferable that the primary tempering is gradually cooled after heating and holding at 550 to 615 ° C., and the secondary tempering is preferably heated and held at 620 to 670 ° C. Also, at the tempering temperature, the high pressure side is preferably tempered at a higher temperature than the low pressure side.
以上のように、高圧部においてクリープ破断強度が高く、又、低圧最終段部において引張強度及び衝撃値が高い両者の特性を備えたロータシャフトを得ることができ、この高低圧一体型ロータシャフトにおいて最終段ブレードとして翼部長さを50サイクル発電に対しては41インチ以上好ましくは43インチ以上、60サイクル発電に対しては34インチ以上好ましくは35インチ以上の長さのものを植設することができる。 As described above, it is possible to obtain a rotor shaft having both the high creep rupture strength at the high pressure portion and the high tensile strength and impact value at the low pressure final stage portion. A blade having a blade length of 41 inches or more, preferably 43 inches or more for 50-cycle power generation, or 34 inches or more, preferably 35 inches or more for 60-cycle power generation, is used as the final stage blade. it can.
本発明によれば、高圧部において優れた高温クリープ強度を有し、又、低圧最終設部において優れた引張強度と低温靱性を有し、低圧最終段部に植設される動翼としてマルテンサイト鋼を用いた翼部長さで、3600rpm蒸気タービンでは914mm(36")以上、3600rpm蒸気タービンでは1092mm(43")以上の長翼化が可能である高低圧一体型蒸気タービンロータとその製造法及び高低圧一体型蒸気タービンとその製造法を提供することができる。 According to the present invention, martensite has a high temperature creep strength at a high pressure part, and has an excellent tensile strength and low temperature toughness at a low pressure final installation part. High and low pressure integrated steam turbine rotor, which can be made longer than 914 mm (36 ") in a 3600 rpm steam turbine and longer than 1092 mm (43") in a 3600 rpm steam turbine, and its manufacturing method, A high-low pressure integrated steam turbine and a manufacturing method thereof can be provided.
図1は、本発明に係る定格出力125MW、回転数3000rpmの再熱型高低圧一体型蒸気タービンの全体構成図である。538℃、126atgの蒸気は入口21から入り、高低圧一体型ロータシャフトの高圧部を通って温度367℃、38atgとなって高圧蒸気出口22より出て、更に再熱器により538℃、35atgに加熱された蒸気が再熱蒸気入口23より入り高低圧一体型ロータシャフト11の中圧部へと入るとともに低圧部及び低圧最終段部へと通り、約46℃、0.1atgの蒸気として出口より排出される再熱型のものである。高圧蒸気出口22から出た蒸気は一部他の熱源として使用される。又、蒸気温度として566℃及び593℃においても同様に構成される。
FIG. 1 is an overall configuration diagram of a reheat type high / low pressure integrated steam turbine having a rated output of 125 MW and a rotational speed of 3000 rpm according to the present invention. Steam at 538 ° C. and 126 atg enters from the
本発明に係る再熱型高低圧一体型蒸気夕一ビンは高低圧一体型ロータシャフト11に植設されたブレードを高圧側6段、中圧側4段、低圧側4段の14段備え、高圧側の段数が中圧側及び低圧側より多く、順次中圧側及び低圧側に段数が少なくなっている。高圧蒸気は蒸気のコントロールバルブ20を通って蒸気入口21より前述の如く538℃、169atgの高温高圧側に流入する。高圧蒸気は入口21より一方向に流れ、高圧蒸気出口22より出て、再び538℃に加熱されて再熱蒸気入口23より中圧夕一ビン部に送られる。中圧夕一ビン部に入った蒸気は低圧タービン部へと送られるとともに低圧蒸気入口からも蒸気が送られる。そして蒸気温度33℃、722mHgとなって最終段ブレード12より排出される。
The reheat type high / low pressure integrated steam evening bin according to the present invention comprises 14 stages of blades implanted on the high / low pressure integrated
本発明に係る高低圧一型体ロータシャフト11は538℃蒸気から33℃の温度までさらされるので、後述する高圧側部分と低圧最終段部とで異なった合金組成と特性を有するNi−Cr−Mo−V低合金鋼の鍛鋼が用いられる。高低圧一体型ロータシャフト11の低圧最終段ブレード12の植込み部はディスク状になっており、高低圧一体型ロータシャフト11より一体に切削されて製造される。ディスク部の長さはブレードの長さが短いほど長くなり、振動を少なくするようになっている。
Since the high and low pressure one-
蒸気入口に対し高圧タ一ビン部のブレードは5段以上の7段あり、初段から最終段の前まではほぼ同じ間隔で配置される。更にブレード植込み部の軸方向の幅は初段及び最終段が最も厚く、初段と最終段を除きほぼ同じ厚さである。中圧タービン部は6段あり、ブレード中心間間隔は初段と2段目までが最も大きく、2段目以降最終段までほぼ同じ間隔である。蒸気入口に対して低圧タ一ビン部のブレードは5段である。中心部での間隔は初段から最終段にかけて徐々に広くなる。ブレード植込み部の軸方向の幅は最終段が最も厚く、最終段より上流側に向って段階的に小さくなる。ブレードの翼部長さは低圧側夕一ビン部が初段から最終段にかけて徐々に大きくなり、最終段の翼部長さは43インチ以上の長さを有する。中圧側夕一ビン部のブレードの翼部長さは初段より最終段にかけて除々に大きくなる。内部ケーシング24、外部ケーシング25である。
The blades of the high-pressure turbine bin section with respect to the steam inlet have seven stages of five stages or more, and are arranged at substantially the same interval from the first stage to the last stage. Furthermore, the axial width of the blade implantation portion is the largest in the first stage and the last stage, and is substantially the same except for the first stage and the last stage. The intermediate pressure turbine section has six stages, and the center distance between the blade centers is the largest in the first stage and the second stage, and is almost the same distance from the second stage to the last stage. There are five stages of blades in the low pressure turbine bin with respect to the steam inlet. The interval at the center gradually increases from the first stage to the last stage. The width in the axial direction of the blade implantation portion is the thickest at the final stage and gradually decreases toward the upstream side from the final stage. The blade length of the blade gradually increases from the first stage to the last stage in the low-pressure side evening bin, and the blade length of the last stage has a length of 43 inches or more. The blade length of the blade on the medium pressure side evening bin section gradually increases from the first stage to the last stage. An
図2は、本発明の高低圧一体型蒸気タービン用ロータシャフトの製造に係るインゴットの形状を示す斜視図である。本実施例のインゴットは、表1に示す高低圧段に記載の合金組成を有する鋼をアーク溶解炉にて溶解後、取鍋に注湯し、次いで取鍋の下部より別の取鍋に注湯して除滓した後、Arガスを下部より吹き込み非金属介在物を浮き上がらせるとともに真空にして精錬を行い、造塊後、900〜1150℃で熱間鍛造を行ったものである。 FIG. 2 is a perspective view showing the shape of an ingot according to the manufacture of the rotor shaft for a high and low pressure integrated steam turbine of the present invention. In the ingot of this example, steel having the alloy composition shown in Table 1 shown in Table 1 was melted in an arc melting furnace, poured into a ladle, and then poured into another ladle from the bottom of the ladle. After removing with hot water, Ar gas was blown in from the bottom to raise non-metallic inclusions, and vacuuming was performed for refining. After ingoting, hot forging was performed at 900 to 1150 ° C.
図2に示すように、前述のインゴットに機械加工を行い、低圧最終段相当部をやや径を小さくして、その部分に添加材のNi線7を軸方向にスポット溶接で溶接し、図2に示す矢印の方向に示すように、低圧最終段部から高圧側部分に亘って全体をエレクトロスラグ溶解を施し、表1に示す合金組成を有する高低圧段及び低圧最終段の供試鋼を溶製した。表1の合金組成は、いずれも中心部の値である。 As shown in FIG. 2, the above-mentioned ingot is machined, the diameter corresponding to the low-pressure final stage is slightly reduced, and the Ni wire 7 of the additive material is welded to the part by spot welding in the axial direction. As shown in the direction of the arrows shown in Fig. 1, the entire low-pressure final stage part to the high-pressure side part is subjected to electroslag melting, and the high-low pressure stage and low-pressure final stage test steels having the alloy compositions shown in Table 1 are melted. Made. All the alloy compositions in Table 1 are the values at the center.
表2は、供試鋼の機械的性質試験結果を示すものである。表2に示すように、供試鋼の高圧、低圧及び低圧最終段にかけて順に0.02%耐力及び引張強さが高くなり、伸び率及び絞り率が低くなっており、更に50%脆性破面遷移温度(℃)が順に低くなって、特に低圧最終段においては−10℃の高い低温靭性を維持しながら高い0.02%耐力850N/mm2及び引張強さ1038N/mm2が得られることが分かる。 Table 2 shows the mechanical property test results of the test steels. As shown in Table 2, the 0.02% proof stress and tensile strength increased in the order of the high pressure, low pressure, and low pressure final stage of the test steel, the elongation and squeezing ratio decreased, and the 50% brittle fracture surface. The transition temperature (° C.) decreases in order, and in the low-pressure final stage, a high 0.02% proof stress 850 N / mm 2 and a tensile strength 1038 N / mm 2 are obtained while maintaining a high low temperature toughness of −10 ° C. I understand.
図4は、低圧部3と低圧最終段部4の各部分(a)及び(a)のA−A断面の各位置についてNi量の含有量の分析を行った各位置を示す断面図である。
FIG. 4 is a cross-sectional view showing each position where the analysis of the Ni content is performed for each position of the low-
表3が図4(a)及び表4が図4(b)の各位置でのNi含有量を示すものである。表3に示すように、本実施例における低圧最終段端部からの軸方向の組成から分かるように、合金組成の傾斜領域は、Ni含有量が前述の高低圧段の含有量にほぼ達する200〜300mmの間であり、傾斜領域を小さくすることができた。 Table 3 shows the Ni content at each position in FIG. 4A and FIG. 4B. As shown in Table 3, as can be seen from the composition in the axial direction from the end of the low-pressure final stage in this example, in the gradient region of the alloy composition, the Ni content almost reaches the content of the above-described high-low pressure stage. It was between ˜300 mm, and the inclined area could be reduced.
本実施例では、低圧最終段の長翼材として、重量比で、C0.16〜0.40%、Si0.25%以下、Mn0.90%以下、Cr8.0〜13.0%、Ni2〜3%、Mo1.5〜3.0%、V0.05〜0.35%、Nb及びTaの一種又は二種の合計量が0.02〜0.20%、及びN0.02〜0.10%を含有するマルテンサイト鋼からなり、全焼戻`しマルテンサイト組織とし、室温の引張強さは120kgf/mm2以上、好ましくは128.5kgf/Imm2以上である。各元素の含有量を重量%として計算されるCr当量を4〜10に成分調整することが好ましい。 In this example, as the long blade material of the low-pressure final stage, by weight ratio, C0.16-0.40%, Si0.25% or less, Mn0.90% or less, Cr8.0-13.0%, Ni2- 3%, Mo 1.5 to 3.0%, V 0.05 to 0.35%, the total amount of one or two of Nb and Ta is 0.02 to 0.20%, and N 0.02 to 0.10 % Martensitic steel, which has a fully tempered martensitic structure, and has a room temperature tensile strength of 120 kgf / mm 2 or more, preferably 128.5 kgf / Imm 2 or more. It is preferable to adjust the component of Cr equivalent calculated to 4 to 10 with the content of each element as weight%.
調質熱処理として、溶解・鍛造後に、1000〜1100℃(好ましくは1000〜1050℃)で、好ましくは0.5〜3時間加熱保持後室温まで急冷する(特に油焼入れが好ましい)焼入れを行い、次いで、550〜620℃で焼戻し、特に550℃〜570℃で、好ましくは1〜6時間加熱保持後室温まで冷却する1次焼戻しと、560℃〜590℃で好ましくは1〜6時間加熱保持後室温まで冷却する2次焼戻しの2回以上の焼戻し熱処理が施されるのが好ましい。 As the tempering heat treatment, after melting and forging, quenching is performed at 1000 to 1100 ° C. (preferably 1000 to 1050 ° C.), preferably heating and holding for 0.5 to 3 hours and then rapidly cooling to room temperature (especially oil quenching is preferable) Next, tempering at 550 to 620 ° C., especially 550 ° C. to 570 ° C., preferably 1 to 6 hours after heating and then cooling to room temperature, and 560 to 590 ° C., preferably 1 to 6 hours after heating and holding Two or more tempering heat treatments of secondary tempering to cool to room temperature are preferably performed.
本実施例では、低圧最終段翼部長さは、914mm(36")以上、好ましくは965mm(38")以上にした60サイクル発電用の3600rpm蒸気タービン、1092mm(43")以上、好ましくは1168mm(46")以上にした50サイクル発電用の3000rpm蒸気タービンにし、〔翼部長さ(インチ)×回転数(rpm)〕値を125,000以上、好ましくは138000以上としたものである。 In this embodiment, the low-pressure final stage blade length is 914 mm (36 ") or more, preferably 965 mm (38") or more, a 3600 rpm steam turbine for 60 cycle power generation, 1092 mm (43 ") or more, preferably 1168 mm ( 46 ") is a 3000 rpm steam turbine for 50 cycle power generation, and the value of [blade length (inch) × rotation speed (rpm)] is 125,000 or more, preferably 138000 or more.
以上、本実施例によれば、高低圧一体型蒸気タービン用ロータシャフトとその製造法においては、高圧部において優れた高温クリープ強度を有し、又、低圧最終段部において優れた引張強度と低温靱性を有するので、低圧最終段部に植設される動翼としてマルテンサイト鋼を用いた翼部長さで、3600rpm蒸気タービンでは914mm(36")以上、3600rpm蒸気タービンでは1092mm(43")以上の長翼化が可能であり、熱効率の優れた高低圧一体型蒸気タービンを提供することができる。 As described above, according to the present embodiment, the high-low pressure integrated steam turbine rotor shaft and its manufacturing method have excellent high-temperature creep strength at the high-pressure part, and excellent tensile strength and low-temperature at the low-pressure final stage part. Since it has toughness, the blade length using martensite steel as the moving blade implanted in the low-pressure final stage portion is 914 mm (36 ") or more in the 3600 rpm steam turbine and 1092 mm (43") or more in the 3600 rpm steam turbine. It is possible to provide a high and low pressure integrated steam turbine that can be made longer blades and has excellent thermal efficiency.
1…高圧部、2…中圧部、3…低圧部、4…低圧最終段部、5…軸部、6フランジ、7…Ni線、11…高低圧一体型蒸気タービン用ロータシャフト、12…低圧最終段ブレード、24…内部ケーシング、25…外部ケーシング、26…軸受け。
DESCRIPTION OF
Claims (20)
In the manufacturing method of a high-low pressure integrated steam turbine comprising a single casing for manufacturing a funnel shaft that is integrally formed across a high-pressure side portion and a low-pressure final stage portion and in which a moving blade is implanted, the method for manufacturing the rotor shaft The manufacturing method of the rotor shaft for high-low pressure integrated steam turbines in any one of Claims 7-19 WHEREIN: The manufacturing method of the high-low pressure integrated steam turbine characterized by the above-mentioned.
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JPH09194946A (en) * | 1996-11-29 | 1997-07-29 | Japan Steel Works Ltd:The | Production of high-low pressure integrated type turbine rotor |
JP2001050007A (en) * | 1999-08-04 | 2001-02-23 | Toshiba Corp | High/low pressure turbine rotor or high/middle/low pressure turbine rotor, manufacturing method for the same, and integral-type steam turbine |
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JPH09194946A (en) * | 1996-11-29 | 1997-07-29 | Japan Steel Works Ltd:The | Production of high-low pressure integrated type turbine rotor |
JP2001050007A (en) * | 1999-08-04 | 2001-02-23 | Toshiba Corp | High/low pressure turbine rotor or high/middle/low pressure turbine rotor, manufacturing method for the same, and integral-type steam turbine |
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JP2011007093A (en) * | 2009-06-25 | 2011-01-13 | Hitachi Ltd | Turbine rotor blade |
CN115161550A (en) * | 2022-06-01 | 2022-10-11 | 江阴兴澄特种钢铁有限公司 | Steel for high-strength fastener for large hydraulic impact crusher and manufacturing method thereof |
CN115161550B (en) * | 2022-06-01 | 2023-10-20 | 江阴兴澄特种钢铁有限公司 | High-strength fastener steel for large hydraulic impact crusher and manufacturing method thereof |
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