EP2872664A1 - Austenitische stahllegierung mit ausgezeichneter zeitstandfestigkeit sowie oxidations- und korrosionsbeständigkeit bei erhöhten einsatztemperaturen - Google Patents

Austenitische stahllegierung mit ausgezeichneter zeitstandfestigkeit sowie oxidations- und korrosionsbeständigkeit bei erhöhten einsatztemperaturen

Info

Publication number
EP2872664A1
EP2872664A1 EP13753262.8A EP13753262A EP2872664A1 EP 2872664 A1 EP2872664 A1 EP 2872664A1 EP 13753262 A EP13753262 A EP 13753262A EP 2872664 A1 EP2872664 A1 EP 2872664A1
Authority
EP
European Patent Office
Prior art keywords
steel
steel alloy
oxidation
weight
alloy according
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.)
Withdrawn
Application number
EP13753262.8A
Other languages
German (de)
English (en)
French (fr)
Inventor
Juliane Mentz
Michael Spiegel
Joachim Konrad
Patrick SCHRAVEN
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzgitter Mannesmann Stainless Tubes GmbH
Original Assignee
Salzgitter Mannesmann Stainless Tubes GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Salzgitter Mannesmann Stainless Tubes GmbH filed Critical Salzgitter Mannesmann Stainless Tubes GmbH
Publication of EP2872664A1 publication Critical patent/EP2872664A1/de
Withdrawn legal-status Critical Current

Links

Classifications

    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12292—Workpiece with longitudinal passageway or stopweld material [e.g., for tubular stock, etc.]

Definitions

  • Austenitic steel alloy with excellent creep rupture strength and oxidation and corrosion resistance at elevated service temperatures
  • the invention relates to an austenitic steel alloy with excellent
  • the invention relates to a heat-resistant austenitic material for the production of pipes, sheets or as a forging material z.
  • a heat-resistant austenitic material for the production of pipes, sheets or as a forging material z.
  • a heat-resistant austenitic material for the production of pipes, sheets or as a forging material z.
  • for seamless superheater pipes in highly efficient new-generation power plants suitable for steam temperatures up to 750 ° C.
  • steam temperatures up to 750 ° C.
  • Power generation in power plants is therefore increasingly the requirement to increase the steam temperature up to 700 ° C and above and also the vapor pressure in the boiler.
  • Heat exchanger tubes at these high operating temperatures are sufficient creep strength, especially in combination with high oxidation resistance in water vapor and corrosion resistance in the presence of flue gas and ashes.
  • power plants are generally based either on ferritic, ferritic / martensitic or austenitic iron-based alloys or nickel-base alloys.
  • Chromium-rich ferritic steel is significantly less expensive compared to austenitic steel and, moreover, has a higher coefficient of thermal conductivity and a lower thermal expansion coefficient. Also owns
  • chromium-rich ferritic steel also has a high oxidation resistance, which is advantageous for hot steam use z. B. in heaters or boilers.
  • creep strengths of 10 5 hours at 700 ° C for a load of 100 MPa must be achieved without breakage.
  • the known materials which are available up to about 620 ° C or 650 ° C application temperature are ferritic / martensitic steels with Cr contents of z. B. 8 to 15%. These materials usually have other expensive alloying additions or are also not suitable for use in temperature ranges above 620 ° C.
  • Austenitic steels for use in steam boilers with steam temperatures up to 700 ° C and above are z. B. from DE 60 2004 002 492 T2.
  • the creep resistance is achieved in particular by an addition of titanium and oxygen within the specified limits.
  • a disadvantage of this steel is the still insufficient oxidation resistance in water vapor and lack of resistance to flue gas corrosion at these high levels
  • the object of the invention is to provide an alloy for an austenitic steel, which satisfies the stated requirements with respect to creep rupture strength and oxidation and corrosion resistance even at operating temperatures up to about 750 ° C and above. Another object is, from this steel alloy workpieces such.
  • Remaining iron with impurities due to melting as well as optional addition of rare earths and reactive elements such as Ce, Hf, La, Re, Sc and / or Y up to a total of 1%.
  • the austenitic high temperature alloy according to the present invention has excellent creep properties as well as good oxidation resistance in water vapor and corrosion resistance in flue gas.
  • the alloy concept differs fundamentally from the known ones
  • the reinforcement of the austenitic matrix against dislocation creep occurs in known austenitic materials up to temperatures of 650 ° C sufficiently by M23C6 on the grain boundaries and finely divided carbides and nitrides
  • the coarsening of sigma phase excreted in the grain causes rapid after initially good creep behavior
  • Creep strength and the oxidation and corrosion resistance at elevated temperatures can only be achieved by avoiding the above-described effects of grain boundary weakening and coarsening of the excreted in the grain sigma phase.
  • the present alloy therefore makes essential use of the finely divided sigma phase precipitated in the grain as reinforcing component in combination with the components M 2 3C 6 and further finely divided carbides, carbonitrides and nitrides, especially of niobium, which have precipitated in the grain and on the grain boundaries, in order to increase the creep rupture strength.
  • Austenitic matrix microstructure with primary niobium carbonitrides (Nb (C, N)) is formed. After heat treatment at 700 ° C or 740 ° C for 4000 h or im
  • FIG. 1 schematically shows the microstructure of the alloy according to the invention after annealing or creep rupture test.
  • Table 1 Composition of the investigated alloys (% by weight)
  • the sum amount of molybdenum, chromium and silicon should be at least 29% by weight.
  • the upper limit of the chromium content is lowered to 30% for the limitation of the sigma phase content.
  • the adjustment of the nickel content is carried out to stabilize the austenitic structure.
  • the upper limit can be lowered here to 35%, which results in a further improvement of the corrosion properties in sulfur-containing flue gases and under sulphate-containing deposits.
  • Optimal properties with regard to creep rupture strength and corrosion are to be set with further limited element limits.
  • the contents of molybdenum are limited to 2 - 5% and silicon to 0, 1 - 1% with regard to an optimal amount and distribution of the sigma phase.
  • the limitation of Nb (0.4-1%), N (0.05-0.12%) and C (0.05-0.12%) has a positive effect on the amount of niobium carbonitride at high temperature ( Grain boundary pinning) on the one hand and the amount and distribution of M23C6 and other carbides, carbonitrides and nitrides at operating temperature on the other.
  • the limitation of the upper limits also has a positive effect on reducing the tendency to segregation and on the processability of the steel.
  • Carbon The carbon content is an integral part of the
  • the upper limit is set at 0.15% by weight and the lower limit is set at 0.02% by weight.
  • Silicon Silicon is needed to increase corrosion resistance and kinetically accelerate sigma phase excretion. A content of at least 0.1% by weight has proved to be advantageous. The weldability is adversely affected by silicon, in addition, silicon stabilizes the Laves phase, which sets by precipitation chromium, so that an upper limit of 2 wt.% Should not be exceeded.
  • Manganese Manganese is a cheap element that is the austenitic matrix of the
  • Chromium oxides in water vapor due to the formation of ternary Mn-Cr oxides Chromium oxides in water vapor due to the formation of ternary Mn-Cr oxides.
  • Manganese content is kept low to avoid accelerated oxidation in water vapor and flue gas. In addition, increased manganese content degrades creep resistance. A content of max. 2.0% by weight is not considered harmful.
  • Chromium The oxidation resistance in water vapor but especially the
  • Chromium is also necessary for the formation of carbides M 2 3C 6 and for the separation of finely divided sigma phase. Since chromium is set by the precipitates, a content of at least 25% by weight is required in order to maintain the matrix concentration necessary for corrosion resistance. In conjunction with molybdenum within the specified limits, the dissolution of reinforcing M 2 3C 6 carbides at the grain boundary in favor of brittle sigma phase is additionally prevented. At high chromium contents, however, the occurrence of ⁇ -ferrite and, consequently, coarse-grained sigma phase is to be expected more frequently. The maximum chromium content is therefore limited to 33% by weight.
  • Nickel is a necessary element for maintaining the austenitic structure and the associated strength benefits, such as creep resistance. In combination with chromium, nickel has a clearly positive effect on the resistance to steam oxidation.
  • Resistance in sulfur-containing flue gases is rather negatively influenced by high contents of nickel, so that at most 38% by weight of nickel should be added.
  • the lower limit should not be less than 22% by weight, since due to the high chromium and molybdenum content, the austenitic matrix should be stabilized against ⁇ -ferrite.
  • Molybdenum The alloying of molybdenum is done to increase the creep strength by solid solution hardening. In addition, a not too high content of molybdenum promotes resistance to chloride-containing gases and ashes. Molybdenum stabilizes the sigma phase in addition to M 23 C 6 and should therefore not fall below a minimum content of 1% by weight. According to the invention, a molybdenum content of up to 6% by weight in combination with chromium and boron hinders the dissolution of reinforcing M 2 3C 6 carbides at the grain boundary in favor of a brittle sigma phase. At the same time molybdenum promotes the excretion of finely divided sigma phase in the grain to increase the
  • Creep resistance Higher contents of molybdenum than 6% by weight cause the formation of too high a content of sigma phase and are furthermore to be avoided because of the tendency of molybdenum to segregate.
  • Tungsten can be alloyed as an optional element and causes accelerated oxidation in water vapor and corrosion under ash covers. Therefore, the proportion should not exceed 2% by weight. At the same time tungsten causes an increase in the creep rupture strength by solid solution hardening and
  • Niobium The precipitation of hardening niobium carbides, niobium carbonitrides and
  • Niobium nitrides in the grain leads to a significant increase in creep rupture strength at application temperatures.
  • niobium acts through the use of
  • Hot forming and weldability The upper limit of 1.5% by weight should therefore not be exceeded. At least about 0.4 weight percent is required to effectively precipitate carbides and nitrides. For an effective precipitate size, the Nb, N and C content must be exactly matched as described above.
  • Titanium, tantalum, vanadium Even precipitates involving titanium, tantalum and / or vanadium can lead to a significant increase in zeistandfestmaschine. To avoid accelerated oxidation or sulfur corrosion, however, the upper limit is set to 0.5% by weight.
  • Nitrogen increases the creep rupture strength by precipitation of nitrides and must therefore be as described above depending on the carbon and
  • Niobium content be alloyed; Nitrogen also stabilizes the austenitic matrix.
  • the lower limit for nitrogen is therefore set at 0.01% by weight.
  • a high nitrogen content causes reduced toughness and ductility and reduces hot workability. Therefore, an upper limit of 0.2% by weight is set.
  • Cobalt Optional addition of Cobalt will increase the
  • Microstructure remain, so an upper limit of 5 wt.% Is set.
  • Copper can optionally be alloyed and used as a further hardening mechanism for the creep rupture strength (precipitation of a Cu phase). Higher levels of copper reduce processability to give an upper limit of 5 wt%.
  • Rare Earths and Reactive Elements The optional addition of rare earths and reactive elements such as Ce, Hf, La, Re, Sc and / or Y can be used to adjust specific properties such as. B. increased thermal shock resistance in levels of up to 1 wt.% Take place.
  • Figures 3 and 4 represent the time-stretching behavior on the basis of strain rates at 740 and 700 ° C.
  • Heat exchanger tubes can be used in the power plant area, but their use is not limited thereto. In addition to the production of pipes that can be seamlessly extruded, hot and cold rolled or welded, this is
  • Tool steels can be used, with their field of application via pressure vessels, Boilers, turbines, nuclear power plants or the chemical apparatus construction, that extends to all areas with corresponding requirements at elevated temperature.
  • the steel alloy according to the invention is particularly advantageous because of the excellent creep strength, corrosion and oxidation properties up to temperatures of 750 ° C or above, the use of this steel, for example, even at temperatures above 600 ° C advantageous if it is more on the Strength of the material arrives.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
EP13753262.8A 2012-07-13 2013-06-27 Austenitische stahllegierung mit ausgezeichneter zeitstandfestigkeit sowie oxidations- und korrosionsbeständigkeit bei erhöhten einsatztemperaturen Withdrawn EP2872664A1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102012014068.1A DE102012014068B3 (de) 2012-07-13 2012-07-13 Austenitische Stahllegierung mit ausgezeichneter Zeitstandfestigkeit sowie Oxidations- und Korrosionsbeständigkeit bei erhöhten Einsatztemperaturen
PCT/DE2013/000369 WO2014008881A1 (de) 2012-07-13 2013-06-27 Austenitische stahllegierung mit ausgezeichneter zeitstandfestigkeit sowie oxidations- und korrosionsbeständigkeit bei erhöhten einsatztemperaturen

Publications (1)

Publication Number Publication Date
EP2872664A1 true EP2872664A1 (de) 2015-05-20

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Application Number Title Priority Date Filing Date
EP13753262.8A Withdrawn EP2872664A1 (de) 2012-07-13 2013-06-27 Austenitische stahllegierung mit ausgezeichneter zeitstandfestigkeit sowie oxidations- und korrosionsbeständigkeit bei erhöhten einsatztemperaturen

Country Status (9)

Country Link
US (1) US20150203944A1 (ko)
EP (1) EP2872664A1 (ko)
JP (1) JP2015528057A (ko)
KR (1) KR20150023935A (ko)
CN (1) CN104718306A (ko)
BR (1) BR112015000274A2 (ko)
DE (1) DE102012014068B3 (ko)
UA (1) UA113659C2 (ko)
WO (1) WO2014008881A1 (ko)

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CN104264031B (zh) * 2014-09-15 2017-01-11 奉化市金燕钢球有限公司 一种不锈轴承钢制备方法
CN104862572B (zh) * 2015-04-30 2017-10-31 宝山钢铁股份有限公司 一种高强度高延伸率的高合金钢及其制造方法
JP6369632B2 (ja) * 2015-06-15 2018-08-08 新日鐵住金株式会社 高Ｃｒ系オーステナイトステンレス鋼
EP3333277B1 (en) 2015-08-05 2019-04-24 Sidenor Investigación y Desarrollo, S.A. High-strength low-alloy steel with high resistance to high-temperature oxidation
CN105296890A (zh) * 2015-10-13 2016-02-03 广东华鳌合金新材料有限公司 一种抗硫腐蚀的耐热合金及其棒材生产方法
JP6688598B2 (ja) * 2015-11-11 2020-04-28 三菱日立パワーシステムズ株式会社 オーステナイト鋼およびそれを用いたオーステナイト鋼鋳造品
DE102017108543B4 (de) 2016-04-23 2022-04-28 Oleg Tchebunin Senkrechtstartendes Flugzeug, dessen Antrieb Drehkolbenkraftmaschinen mit kontinuierlichem Brennprozess und Schubrichtungsschwenkanlagen aufweist
CN106381452B (zh) * 2016-09-07 2018-01-16 大连理工大学 一种700℃下高组织稳定性的耐热奥氏体不锈钢
JP6795038B2 (ja) * 2016-10-03 2020-12-02 日本製鉄株式会社 オーステナイト系耐熱合金およびそれを用いた溶接継手
CN106929739A (zh) * 2017-04-20 2017-07-07 天津达祥精密工业有限公司 一种微合金化铬镍系奥氏体耐热钢及其制备方法和应用
CN106893949B (zh) * 2017-04-20 2019-01-25 华能国际电力股份有限公司 一种奥氏体耐热钢及其制备方法
CN107574352A (zh) * 2017-09-12 2018-01-12 江苏金利化工机械有限公司 一种可硬化的奥氏体合金
CN109778048B (zh) * 2019-01-30 2021-02-05 江苏飞跃机泵集团有限公司 一种高硬度、耐蚀的Ni-Cr-Fe合金及其制备方法
CN111500940B (zh) * 2020-06-08 2020-10-16 南京工程学院 具有抑制摩擦火花特性的合金钢锻造制动盘及其制造方法
CN114086078A (zh) * 2020-08-25 2022-02-25 华为技术有限公司 Fe-Mn-Al-C系轻质钢及其制备方法、终端、钢结构件和电子设备
CN112575248A (zh) * 2020-10-29 2021-03-30 江苏新核合金科技有限公司 一种核电堆内构件导向结构用合金材料及其制备方法
CN113151747A (zh) * 2021-04-27 2021-07-23 中国核动力研究设计院 一种耐高温腐蚀的含铝奥氏体不锈钢及制备方法
SE545185C2 (en) * 2021-09-07 2023-05-09 Alleima Emea Ab An austenitic alloy object
CN114000027B (zh) * 2021-09-30 2022-09-16 江西宝顺昌特种合金制造有限公司 Uns n08120锻环及其制造方法
CN116121667A (zh) * 2021-11-14 2023-05-16 重庆三爱海陵实业有限责任公司 气门及其耐高温合金

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Publication number Publication date
US20150203944A1 (en) 2015-07-23
DE102012014068B3 (de) 2014-01-02
WO2014008881A1 (de) 2014-01-16
KR20150023935A (ko) 2015-03-05
JP2015528057A (ja) 2015-09-24
BR112015000274A2 (pt) 2017-06-27
UA113659C2 (uk) 2017-02-27
CN104718306A (zh) 2015-06-17

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