EP1602742A1 - Hochfester Stahl für die Herstellung von großen Schmiedestücken, insbesondere von Kurbelwellen - Google Patents

Hochfester Stahl für die Herstellung von großen Schmiedestücken, insbesondere von Kurbelwellen Download PDF

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Publication number
EP1602742A1
EP1602742A1 EP05011252A EP05011252A EP1602742A1 EP 1602742 A1 EP1602742 A1 EP 1602742A1 EP 05011252 A EP05011252 A EP 05011252A EP 05011252 A EP05011252 A EP 05011252A EP 1602742 A1 EP1602742 A1 EP 1602742A1
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EP
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Prior art keywords
steel
strength
crankshaft
forging
scaled
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Granted
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EP05011252A
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English (en)
French (fr)
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EP1602742B1 (de
Inventor
Shogo Fukaya
Yasunori Kagawa
Nobuyuki Fujitsuna
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Kobe Steel Ltd
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Kobe Steel Ltd
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    • 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
    • C21D9/30—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for crankshafts; for camshafts
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

Definitions

  • the present invention relates to high-strength steels for large-scaled forgings, such as for manufacturing an integrated type of forged steel assembled large-scaled crankshaft, which is suitable for use in a diesel engine or the like used in a ship or generator, and to crankshafts using the same. More particularly, the invention relates to a high-strength steel for a large-scaled forging with the small content of Ni, which is an expensive alloying element, and having high strength at low cost, and to a large-scaled crankshaft which exhibits such properties.
  • 3.5NiCrMo steel or the like which is used in rotors (see, for example, "Tetsu to Hagane", vol. 89 (2003) No. 6) .
  • This steel has the most excellent strength, toughness, and the like, and is used as a rotor (rotating shaft) for a generator which is put under high load.
  • the above type of steel contains the large amount of Ni, which is very expensive, as an alloying element for strengthening and toughing the steel, and is preferably subjected to a two-stage tempering process to ensure toughness, or to a specific prehardening process to minimize the grain size, resulting in a problem of high cost.
  • Cr-Mo steels notably 34CrNiMo6 as defined in a DIN specification, 32CrMo12 as defined in the same, 42CrMo4 as defined in an ISO specification, have been hitherto used as steels for large-scaled crankshafts, which are used for parts of an engine and a transmission mechanism in the ships or the like.
  • These types of steels have the advantage of relatively low cost because they have less content of Ni compared to the above-mentioned 3.5NiCrMo steel. In fact, however, these steels do not meet the recent requirements in terms of strength and toughness, as compared to the above type of steel.
  • the present invention has been accomplished in view of the above-mentioned problems, and it is an object of the invention to provide a high-strength steel for a large-scaled forging which is low in cost as compared to the 3.
  • SNiCrMo steel proposed as the steel for the high-strength Ni-Cr-Mo steel, and which has excellent strength and toughness as compared to the 34CrNiMo6 as defined in the DIN specification which has been put to practical use.
  • a high-strength steel for a large-scaled forging according to the invention which has solved the above-mentioned problems, has the principle that the steel consists essentially of, by mass, (the contents of the following components being expressed in mass % in the same manner) C: 0.30 to 0.50 %, Si: more than 0.15 %, but not more than 0.40 %, Mn: 0.80 to 1.20 %, Ni: 0.80 to 2.5 %, Cr: 1.0 to 3.0%, Mo: 0.35 to 0.70 %, V: 0.10 to 0.25%, and balance: Fe and unavoidable impurities.
  • a grain size in a metal structure of the steel is preferably an ASTM grain size number ranging from 2 to 6. Further, the high-strength steel for a large-scaled forging of the invention is preferably produced by quenching under 200 °C from austenitizing-temperature and then tempering.
  • crankshaft By forging the above-mentioned high strength steel for a large-scaled forging, a large-scaled crankshaft with desired properties is obtained.
  • a crankshaft is useful as a crankshaft for a diesel engine used in a ship or generator.
  • the Ni content is reduced as compared to that of the 3.5NiCrMo steel which has been proposed as steel for a high-strength Ni-Cr-Mo forging, leading to reduction in cost, while predetermined contents of Si, Mn, Cr, and the like are contained therein, enhancing the strength.
  • the invention can provide the steel for forgings of high quality at low cost.
  • this steel for forgings has very excellent hardenability (quenching ability). That is, this steel has an excellent property that the microstructure can be controlled to that consisting only of bainite and martensite.
  • the steel can be effectively utilized as material for large-scaled forged products.
  • the steel is extremely useful as material for large-scaled crankshafts, including a crankshaft for a diesel engine used in a ship or generator.
  • the inventors have been dedicated themselves to studying the development of steel for a forging in which the amount of Ni contained as an alloying element is reduced as compared to, in particular, 3.5NiCrMo steel known as the high-strength steel for forgings, leading to reduction in cost, and further which has the strength and toughness equivalent to those of the known steel, while being capable of exhibiting excellent hardenability, which is important in manufacturing the large-scaled high-strength forgings.
  • the inventors have found that the amount of Ni serving as a strengthening element in the above-mentioned steel for Ni-Cr-Mo based steels should be reduced as much as possible, while the elements including Si, Mn, Cr, and the like, should be added in appropriate amounts, thereby providing the steel for forgings with extremely excellent hardenability and with the improved strength and toughness to compensate for the shortage of strength caused by the decreased Ni amount, so that the invention has been accomplished.
  • Ni is a very useful element for enhancing the strength and toughness of the Cr-Mo based steel, which has been used as the steel for forgings for multipurpose applications as mentioned above, and for improving the hardenability. For this reason, the Ni is the extremely useful element to the high-class Cr-Mo based steel for forging.
  • the invention has been developed to achieve the following most important aims: to reduce the Ni content as much as possible, and to be capable of ensuring the strength and quenching properties equivalent to those of the conventional steel for Ni-Cr-Mo based steels. In order to accomplish the object of reducing cost by decreasing the amount of Ni, the Ni content is desirably reduced to not more than 2.5 %.
  • the steel for forgings according to the invention is characterized by that the Ni content is restricted as mentioned above, and that instead the alloying elements including Si, Mn, Cr, and the like are added in appropriate amounts.
  • the reasons for restriction of a chemical component composition defined by the invention, including the above-mentioned elements, are as follows:
  • the C is an element contributing to enhancement of the hardenability and improvement of the strength. To ensure enough strength and hardenability, the C needs to be contained in an amount of 0. 30 % or more. The excessive C content, however, extremely decreases the toughness, while enhancing formation of an inverse V-segregation in a large-scaled ingot. Accordingly, the C content is preferably reduced to not more than 0.50 %.
  • Si more than 0.15 %, but not more than 0.40 %
  • the element Si acts as a strength improving element, and needs to be contained in an amount exceeding 0.15 % in order to ensure enough strength.
  • the excessive amount of Si results in formation of the significant inverse V-segregation, making it difficult to obtain clean ingots. Accordingly, the Si content should be not more than 0.40 %.
  • the element Mn is an element contributing to enhancement of the hardenability and improvement of the strength. To ensure enough strength and hardenability, the Mn needs to be contained in an amount of 0.80 % or more. The excessive Mn content, however, enhances the tempering embrittlement. Accordingly, the Mn content needs to be not more than 1.20 %.
  • the element Cr is an element which is useful for enhancement of the hardenability and improvement of the toughness. To sufficiently exhibit these effects, the Cr needs to be contained in an amount of 1.0% or more.
  • the excessive Cr content however, forms inhomogeneous solidification, making it difficult to manufacture the clean steel. Accordingly, the Cr content needs to be not more than 3.0 %.
  • the element Mo is an element which effectively acts to improve all of the hardenability, strength, and toughness. To sufficiently exhibit these effects, the Mo needs to be contained in an amount of 0.35 % or more. If the Mo content is less than the above-mentioned amount, the inverse V-segregation is formed, which is not desirable. In contrast, since the excessive Mo content promotes micro-segregation in the ingots, and the Mo is a heavy element, gravity segregation tends to occur. Accordingly, the Mo content needs to be not more than 0.70 %.
  • V 0.10 to 0.25 %
  • the element V is an element which effectively acts to improve the hardenability and strength even in a small amount. To exhibit these effects, the V needs to be contained in an amount of 0.10% or more. However, since the element V has a low equilibrium distribution coefficient, the excessive V content tends to cause the micro-segregation (normal segregation). Accordingly, the V content needs to be not more than 0.25 %.
  • the steel for forgings used in the invention preferable basic components are as mentioned above.
  • the balance consists essentially of Fe, but the minute amounts of unavoidable impurities (including, for example, P, O, N, Al, or the like) may be allowed to be contained in the steels.
  • the steel for forgings positively containing another element within a range that does not adversely affect the effects of the invention can be employed.
  • the other elements that are allowed to be included in the steel are, for example, Ti, Ca, Mg, S, and the like. From a viewpoint of prevention of formation of rough inclusions, these elements are desirably reduced to not more than about 0.5 % in total.
  • the inventors have fully considered aiming for development of the steel which can ensure enough toughness even in coarse grains, and which suppresses the formation of the remaining austenite in quenching, without needing the special process, such as the two-stage tempering process, for the purpose of ensuring the toughness.
  • the high-strength steel for forgings with the above chemical composition ensures enough toughness even in the metal structure having the grain size of the ASTM grain size No.6 or less, and has only to be subjected to only one-time tempering process.
  • the steel with the ASTM grain size number less than two the grain size is significantly increased, resulting in degradation in toughness of the forged steel.
  • the ASTM grain size number is preferably at least two.
  • a crankshaft for a diesel engine used in a ship or generator has a journal diameter of at least about 150 mm, which is extremely large as compared to that of the vehicle (for example, about 15 mm). Since water quenching leads to a danger of cracking and breaking down in manufacturing the large-scaled forging, quenching of the large-scaled crankshaft is generally performed by oil quenching, polymer quenching, air cooling or the like. In manufacturing the large-scaled crankshaft of interest in the invention, although cooling rate in the quenching depends on a diameter of the crankshaft, it is not more than 50 °C/min in the oil quenching. More specifically, for a crankshaft with a diameter of 500 mm grade, the cooling rate is about 20 °C/min. For a crankshaft with a larger diameter than this (for example, 1000 mm), the cooling rate is much lower.
  • the microstructure is preferably controlled to consist of bainite and martensite.
  • the quenching cooling rate of about 20 °C/min (in the case of oil quenching) so as to apply the steel to the large-scaled crankshaft with a diameter of 150 mm or more
  • the inventors have found out the aforesaid chemical composition.
  • This polymer quenching involves cooling the steel by use of cooling solution which is produced by dissolving organic solvent, such as glycols (for example, diethylene glycol, polyethylene glycol, or the like), into water.
  • organic solvent such as glycols (for example, diethylene glycol, polyethylene glycol, or the like)
  • the polymer quenching is a cooling system useful for prevention of cracks, which might occur in the water quenching, and for achieving the higher cooling rate, for example, the cooling rate of more than 20 °C/min for the relatively large-scaled forgings.
  • the austenitized steel is subjected to quenching to under 200 °C, and then tempering from a viewpoint of completion of the transformation. If the quenching temperature (namely, tempering start temperature) exceeds 200 °C, partially austenite remains without transformation to bainite and martensite, which causes variations in properties.
  • a method of manufacturing the steel for the forging according to the invention is not particularly limited.
  • the steel has only to be adjusted to predetermined chemical compositions, and then to be cast using a high-frequency melting furnace, an electric furnace, a converter, or the like in a normal manner. Performing a vacuum process after adjustment of the compositions is also effective.
  • ingot casting is mainly employed, while, in the case of the relatively small-scaled forging, a continuous casting method can be employed.
  • a method of manufacturing, for example, a crankshaft or the like, using the steel for forgings is not particularly limited.
  • the method may comprise the following steps of: melting steel with a predetermined composition in the electric furnace; removing an impurity element, such as S, and a gas component, such as O, by vacuum refining; ingot-making; forging to a bar after heating the ingot; heating the forged bar after an intermediate inspection and forging it into a shape of a crankshaft; performing heat treatment for obtaining required properties such as quench-hardening and tempering; and finish machining, wherein these steps are carried out in this order.
  • a free forging method (which involves forging a crank arm and a crank pin into one block, and finishing the forged block into the crankshaft shape by gas cutting and machining), and RR and TR forging methods (which involves performing forge processing in such a manner that the center axis of an ingot is aligned with a center axis of a crankshaft) are exemplified as a forge processing method for forging the material into the crankshaft.
  • the latter is more preferable because high cleanness level without segregation can be obtained in the near surface region where high stress is loaded in operation, easily obtaining the crankshaft with excellent strength and fatigue property.
  • the thus-obtained crankshaft is very useful as a crankshaft for a diesel engine used in a ship or generator.
  • a quenching process was carried out which simulated respective heating and cooling rates at a point located 50 mm (which is one tenth of the diameter) below the surface of the crankshaft having the diameter of 500 mm. More specifically, the steel was heated up to 870 °C at a rate of temperature increase of 40 °C/hr using a small-scaled simulate furnace, and kept at the temperature for one hour. (austenitizing process) Then, the steel was cooled at an average cooling rate of 20 °C/min to a temperature ranging from 500 to 870 °C to perform a quenching process.
  • a tempering process was carried out at a temperature ranging from 580 to 630 °C for 13 hours, and cooling was performed by furnace cooling. Thereafter, mechanical properties of each of the thus-obtained steels were evaluated in the following manner.
  • the grain size of the steel was measured based on the ASTM (grain size number).
  • the absorbed energies at tempering temperatures which brought about the strength of around 1000 N/mm 2 are designated as Eu and Ed, and the respective tensile strengths as Su and Sd.
  • samples of tests No. 4 to 12 which meet the range specified by the invention, have the tensile strength of not less than 1000 N/mm 2 .
  • a Charpy absorbed energy of each of these samples vE tends to depend on the Ni content.
  • a relation between an absorbed energy at the strength of 1000 N/mm 2 , into which the determined absorbed energy is converted, and the Ni content is shown in Fig.1. Further, a relation between the Ni content and the grain size number is shown in Fig.2. Fig.1 shows clearly that the steel with the Ni content of not less than 0.80 % and not more than 2.5 % has good impact property. It is generally known that increase in the Ni content improves the toughness of the steel. That is, it has shown that the effect of Ni is not exhibited markedly until the Ni content reaches 0.80 % or more. In contrast, it has shown that when the Ni content is more than 2.5 %, the toughness is lowered.
  • the steel with the grain size number of two or more can ensure the good toughness.
  • toughness improves monotonously as Ni content increases.
  • the upper limit of the range of Ni content 2.5% equals by chance the aforementioned upper limit of Ni content to be considered in terms of cost.
  • the steel is cooled not to room temperature, but to a temperature ranging from 200 to 300 °C, and then a tempering process is successively carried out, from a viewpoint of preventing cracking, which might be caused by deforming and thermal stresses in the quenching and tempering processes.
  • a cause of the influence of the tempering start temperature on the tensile strength in the chemical compositions specified by the invention is not clearly known, but it is considered that the chemical compositions limited within a range specified by the invention form a partial martensitic structure, and not a complete bainitic structure, and that the tempering start temperature has the influence on formation of such a transformed structure.
  • Type of steel Chemical composition (mass %) C Si Mn P S Cu Ni Cr Mo V Al A 0.35 0.24 0.62 0.004 0.003 0.03 1.51 1.49 0.22 0.081 0.003 B 0.28 0.23 1.05 0.005 0.003 0.03 1.52 2.03 0.52 0.21 0.004 C 0.38 0.26 0.77 0.003 0.003 0.03 1.54 2.03 0.53 0.19 0.006 D 0.36 0.22 0.99 0.005 0.003 0.03 0.22 2.92 0.47 0.1 0.005 E 0.36 0.24 0.94 0.005 0.003 0.03 3.05 0.21 0.49 0.11 0.026 F 0.36 0.23 0.98 0.005 0.003 0.03 1.63 1.58 0.48 0.11 0.022 G 0.39 0.2 0.94 0.008 0.003 0.04 0.52 2.9 0.48 0.15 0.018 H 0.38 0.21 1.02 0.008 0.003 0.05 0.82 2.8 0.47 0.16 0.030 I 0.34 0.22 0.98 0.007 0.003 0.04 1.58 1.59 0.49 0.16

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)
  • Forging (AREA)
EP05011252A 2004-06-01 2005-05-24 Hochfester Stahl für die Herstellung von großen Schmiedestücken, insbesondere von Kurbelwellen Expired - Fee Related EP1602742B1 (de)

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JP2004163638A JP4332070B2 (ja) 2004-06-01 2004-06-01 大型鍛鋼品用高強度鋼およびクランク軸
JP2004163638 2004-06-01

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EP1602742A1 true EP1602742A1 (de) 2005-12-07
EP1602742B1 EP1602742B1 (de) 2009-07-15

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KR (1) KR100721645B1 (de)
DE (1) DE602005015383D1 (de)
ES (1) ES2328365T3 (de)

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EP2036992A1 (de) * 2006-06-21 2009-03-18 Kabushiki Kaisha Kobe Seiko Sho Schmiedestahl, herstellungsverfahren dafür und schmiedestück
CN102722762A (zh) * 2011-12-29 2012-10-10 昆明理工大学 高炉/转炉区段排队***解析仿真方法
CN102728772A (zh) * 2012-06-26 2012-10-17 江苏金源锻造股份有限公司 一种大型船用曲轴的锻造方法
CN103233111A (zh) * 2013-04-02 2013-08-07 浙江来源机械有限公司 大直径港机专用高耐磨高强度传输轴制备工艺
CN103352113A (zh) * 2013-06-30 2013-10-16 贵州安大航空锻造有限责任公司 48MnV非调质钢曲轴锻件的热处理方法
EP2671963A1 (de) * 2012-06-06 2013-12-11 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Grosse Stahlschmieden mit hoher festigkeit
US20140345756A1 (en) * 2013-05-21 2014-11-27 General Electric Company Martensitic alloy component and process of forming a martensitic alloy component
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CN105603169A (zh) * 2016-03-07 2016-05-25 江苏大学 大型30CrNi2MoV钢件的短流程制造方法
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US10253398B2 (en) 2013-12-19 2019-04-09 Kobe Steel, Ltd. High-strength steel for steel forgings, and steel forging
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JP6179977B2 (ja) * 2013-05-22 2017-08-16 株式会社日本製鋼所 耐高圧水素環境脆化特性に優れた高強度鋼およびその製造方法
JP6100129B2 (ja) 2013-08-27 2017-03-22 株式会社神戸製鋼所 高強度鋼及び船舶又は発電機のディーゼル機関用クランク軸
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JP2017122500A (ja) 2016-01-08 2017-07-13 株式会社神戸製鋼所 大型クランク軸
JP2017128795A (ja) 2016-01-18 2017-07-27 株式会社神戸製鋼所 鍛造用鋼及び大型鍛鋼品
CN105755236A (zh) * 2016-03-07 2016-07-13 江苏大学 提高35CrNi3MoV钢锻件低温冲击韧性的方法
JP7176877B2 (ja) * 2018-07-23 2022-11-22 山陽特殊製鋼株式会社 耐衝撃性に優れた機械構造用合金鋼

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Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2036992A4 (de) * 2006-06-21 2011-01-26 Kobe Steel Ltd Schmiedestahl, herstellungsverfahren dafür und schmiedestück
US8057737B2 (en) 2006-06-21 2011-11-15 Kobe Steel, Ltd. Forging steel and its manufacturing method, and forged parts
EP2036992A1 (de) * 2006-06-21 2009-03-18 Kabushiki Kaisha Kobe Seiko Sho Schmiedestahl, herstellungsverfahren dafür und schmiedestück
CN102722762A (zh) * 2011-12-29 2012-10-10 昆明理工大学 高炉/转炉区段排队***解析仿真方法
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KR20060046214A (ko) 2006-05-17
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JP2005344149A (ja) 2005-12-15
DE602005015383D1 (de) 2009-08-27
EP1602742B1 (de) 2009-07-15

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