EP1428897A1 - Verfahren zur Herstellung eines Bauteils mit verbesserter Schweissbarkeit und/oder mechanischen Bearbeitbarkeit aus einer Legierung - Google Patents

Verfahren zur Herstellung eines Bauteils mit verbesserter Schweissbarkeit und/oder mechanischen Bearbeitbarkeit aus einer Legierung Download PDF

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Publication number
EP1428897A1
EP1428897A1 EP02027496A EP02027496A EP1428897A1 EP 1428897 A1 EP1428897 A1 EP 1428897A1 EP 02027496 A EP02027496 A EP 02027496A EP 02027496 A EP02027496 A EP 02027496A EP 1428897 A1 EP1428897 A1 EP 1428897A1
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EP
European Patent Office
Prior art keywords
heat treatment
component
welding
alloy
carried out
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Withdrawn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
EP02027496A
Other languages
German (de)
English (en)
French (fr)
Inventor
Nigel-Philip Cox
Dirk Dr. Goldschmidt
Rolf Dr. Wilkenhöner
Konstantin A. Prof. Yushchenko
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.)
Siemens AG
Original Assignee
Siemens AG
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 Siemens AG filed Critical Siemens AG
Priority to EP02027496A priority Critical patent/EP1428897A1/de
Priority to PCT/EP2003/013882 priority patent/WO2004053181A2/de
Priority to EP03782329A priority patent/EP1570098A2/de
Priority to CN200380105754.3A priority patent/CN1726297B/zh
Priority to US10/538,414 priority patent/US20060144477A1/en
Publication of EP1428897A1 publication Critical patent/EP1428897A1/de
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon

Definitions

  • the invention relates to a method for producing a Component with improved weldability and / or machinability from an alloy according to Claim 1.
  • US Pat. No. 5,938,863 discloses a nickel-based superalloy, has the addition of carbides to the Improve fatigue behavior.
  • U.S. Patent 6,120,624 discloses heat treatment of a Nickel based superalloy before welding to make that Formation of cracks in heat treatments after To avoid welding.
  • U.S. Patent 4,579,602 and U.S. Patent 4,574,015 disclose Heat treatments for cast superalloys to achieve this Forging these materials to improve.
  • an alloy component During the manufacture of an alloy component the component has to be manufactured in various intermediate stages to be edited. Often the alloy has not the desired properties to get them optimal to be able to edit.
  • the alloy can be relatively brittle, making mechanical processing (straightening, machining, grinding) difficult. Likewise, cracks or holes often have to be welded, although the alloy is often difficult to weld.
  • the object is achieved by a production method a component with improved weldability and / or machinability from an alloy according to Claim 1.
  • FIG. 1 shows an example of the time profile of the Temperature of an alloy during the manufacturing process.
  • the alloy can be hardened by excretions, for example for example a nickel or cobalt based superalloy.
  • the alloy can form a component from a powder sintered or cast or straightened as a melt to be left frozen. Other types of manufacture are conceivable.
  • the temperature is higher than the melting temperature T M (FIG. 1).
  • T M melting temperature
  • the casting process is followed, for example, by post-compression, in particular directly after the casting process, ie without cooling of the component after the casting.
  • the post-compression is carried out, for example, by hot isostatic pressing (HIP) (area I, FIG. 1) or by sintering in order to close defects such as pores, cavities, etc.
  • HIP hot isostatic pressing
  • the post-compression can also take place after other manufacturing steps.
  • the Components made of this alloy are mechanical processed (e.g. straightened or cutting, grinding Processing) and / or welding repairs are carried out by Faults in the component, especially at room temperature.
  • the microstructure (structure) of the component changed so that the processability of the Alloy is improved compared to the untreated structure.
  • the structural features include the crystal structure, Excretions and secondary phases.
  • the exemplary aging heat treatment can be connected directly to the post-compression process, in particular in the same furnace, or after casting or sintering. There is no or only insignificant cooling of the component (Fig. 1, transition area I, II) If the post-compression process is carried out using a HIP process, the pressure during the improvement heat treatment can remain, be slowly reduced or reduced.
  • the aging heat treatment is done by heating up a certain temperature, possibly with a holding time at this temperature, and for example by a low one Cooling rate of greater than 1 ° C to 5 ° C per minute, in particular from 2 ° C to 3 ° C per minute, e.g. immediately after the Post-compaction process reached (area II, Fig.1).
  • the aging heat treatment becomes an aging of the ⁇ '-phase, whereby the ductility of the Base material is significantly increased.
  • This aging heat treatment improves the weldability of the alloy, in particular at room temperature, compared to the untreated alloy.
  • the improved mechanical ductility of the alloy compared to the untreated alloy makes the component easier to straighten (mechanically deformable) and / or better machinable or grinding.
  • the structure obtained in this way can be used at high temperatures Compared to the structure before the heat treatment worse Have properties.
  • high-strength nickel super alloys such as IN939, Rene80 and IN738LC have not been used so far, particularly for large and thin-walled components such as combustion chamber linings. These alloys have the ⁇ '-phase to increase strength and can now be processed and used with the method according to the invention without restrictions (with welding points).
  • the material of choice was previously Hastelloy X. This material is easier to weld, but has limited high-temperature strength and directionality compared to the other material classes.
  • the component can be used, for example, for solution annealing (1180 ° C for the above-mentioned materials) with subsequent rapid cooling (20 ° - 40 ° C per minute to 800 ° C, then air cooling), i.e. faster than the cooling rate in the improvement heat treatment ,
  • the outdated structure is "erased” again, ie the coarse precipitations at least partially disappear and the component regains its good high-temperature properties in the alloy, for example by adjusting a finely dispersed ⁇ '-structure (rapid cooling).
  • the structure may indicate the area of application of the component better properties than the structure that the component after heat treatment to improve the Processability showed.
  • this ⁇ '-phase is dissolved.
  • the ⁇ '-phase fails and coarsens accordingly.
  • the coarsening not only leads to an increase in the mean diameter of the ⁇ '-phase, but also, for example, to spherodization of the ⁇ '-phase, ie it is less cube-shaped, but more platelet-shaped. Such coarsening leads to increased ductility.
  • a corresponding heat treatment is carried out which changes the microstructure in such a way that it improves the processability of the component, in particular at room temperature.
  • the process to improve the workability of the Alloy can be used for newly manufactured components as well as for components that were in use (refurbishment).
  • the procedure is as follows, for example.
  • the used component is cleaned (removal of oxidation / corrosion products) and stripped, for example. Then the component is assessed, ie the detection of cracks and pores. An aging heat treatment then takes place, which is followed either by welding repair of the cracks and pores at room temperature or by straightening the component. It then takes place if necessary. cold deforming (hammering or hammering) of the welding points created in this way. This is followed, for example, by heat treatment again (for example solution annealing) in order to set the desired finely dispersed y 'structure. If necessary, there is a further post-treatment of the welds, for example a local heat treatment.
  • the solution annealing takes place, for example, at the same temperature as in the aging heat treatment, but with faster cooling, in order to avoid the coarsening of the ⁇ ′ structures. It is cooled so quickly that the ⁇ '-phase is not completely eliminated, but remains at least partially positively dissolved. If necessary, outsourcing can be carried out to remove the desired ⁇ '-structure (fine blocky particles).
  • a type of filler or a filler with the same composition as the component is used.
  • the same type means that it has approximately the same composition as the component or the same high-temperature properties as the base material.
  • the components of the welding filler for example, have the same proportions as the material of the component. Possibly. welding consumables can be dispensed with. In particular, welding additives that are less resistant to high temperatures should be avoided.
  • the welding filler can be hardened by precipitations, ie its strength can be increased, the welding point hardly or not at all reduces the strength of the component.
  • the welding additive should have at least a volume fraction of 35% for the excretions (for example the ⁇ '-phase).
  • the aging temperature of 1180 ° C for IN939 is aware chosen higher than from the prior art (1160 ° C, US-PS 6,120,624).
  • FIG. 2 shows different microstructures Superalloy.
  • the microstructure of the alloy is IN738 shown.
  • Figure 2a shows the alloy with cubic primary ⁇ 'and fine secondary ⁇ '-phase, so that a high-strength Alloy results in a low ductility.
  • Figure 2b shows an outdated microstructure, the one has platelet-shaped ⁇ 'phase, but no secondary ⁇ '-phase. This microstructure has one compared to FIG. 2a increased ductility.

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Powder Metallurgy (AREA)
  • Arc Welding In General (AREA)
  • Heat Treatment Of Steel (AREA)
EP02027496A 2002-12-10 2002-12-10 Verfahren zur Herstellung eines Bauteils mit verbesserter Schweissbarkeit und/oder mechanischen Bearbeitbarkeit aus einer Legierung Withdrawn EP1428897A1 (de)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP02027496A EP1428897A1 (de) 2002-12-10 2002-12-10 Verfahren zur Herstellung eines Bauteils mit verbesserter Schweissbarkeit und/oder mechanischen Bearbeitbarkeit aus einer Legierung
PCT/EP2003/013882 WO2004053181A2 (de) 2002-12-10 2003-12-08 Verfahren zur herstellung eines bauteils mit verbesserter schweissbarkeit und/oder mechanischen bearbeitbarkeit aus einer legierung
EP03782329A EP1570098A2 (de) 2002-12-10 2003-12-08 Verfahren zur herstellung eines bauteils mit verbesserter schweissbarkeit und/oder mechanischen bearbeitbarkeit aus einer legierung
CN200380105754.3A CN1726297B (zh) 2002-12-10 2003-12-08 从合金制备有改善的可焊性和/或机械加工性的部件的方法
US10/538,414 US20060144477A1 (en) 2002-12-10 2003-12-08 Method for the production of a part having improved weldability and/or mechanical processability from an alloy

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP02027496A EP1428897A1 (de) 2002-12-10 2002-12-10 Verfahren zur Herstellung eines Bauteils mit verbesserter Schweissbarkeit und/oder mechanischen Bearbeitbarkeit aus einer Legierung

Publications (1)

Publication Number Publication Date
EP1428897A1 true EP1428897A1 (de) 2004-06-16

Family

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Family Applications (2)

Application Number Title Priority Date Filing Date
EP02027496A Withdrawn EP1428897A1 (de) 2002-12-10 2002-12-10 Verfahren zur Herstellung eines Bauteils mit verbesserter Schweissbarkeit und/oder mechanischen Bearbeitbarkeit aus einer Legierung
EP03782329A Withdrawn EP1570098A2 (de) 2002-12-10 2003-12-08 Verfahren zur herstellung eines bauteils mit verbesserter schweissbarkeit und/oder mechanischen bearbeitbarkeit aus einer legierung

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP03782329A Withdrawn EP1570098A2 (de) 2002-12-10 2003-12-08 Verfahren zur herstellung eines bauteils mit verbesserter schweissbarkeit und/oder mechanischen bearbeitbarkeit aus einer legierung

Country Status (4)

Country Link
US (1) US20060144477A1 (zh)
EP (2) EP1428897A1 (zh)
CN (1) CN1726297B (zh)
WO (1) WO2004053181A2 (zh)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1835040A1 (de) 2006-03-17 2007-09-19 Siemens Aktiengesellschaft Schweisszusatzwekstoff, Verwendung des Schweisszusatzwekstoffes, Verfahren zum Schweissen und Bauteil
EP2182084A1 (de) 2008-11-04 2010-05-05 Siemens Aktiengesellschaft Schweisszusatzwerkstoff, Verwendung des Schweisszusatzwserkstoffes und Bauteil
US7915566B2 (en) 2005-10-24 2011-03-29 Siemens Aktiengesellschaft Weld filler, use of the weld filler and welding process

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100032414A1 (en) * 2007-03-23 2010-02-11 Nikolai Arjakine Inert gas mixture and method for welding
US11515086B2 (en) * 2012-07-12 2022-11-29 Nissan Motor Co., Ltd. Method for manufacturing sintered magnet
US11072044B2 (en) * 2014-04-14 2021-07-27 Siemens Energy, Inc. Superalloy component braze repair with isostatic solution treatment
CN106048484B (zh) * 2016-07-06 2018-02-23 中南大学 一种采用两段阶梯应变速率工艺细化gh4169合金锻件晶粒组织的方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4574015A (en) * 1983-12-27 1986-03-04 United Technologies Corporation Nickle base superalloy articles and method for making
US4579602A (en) * 1983-12-27 1986-04-01 United Technologies Corporation Forging process for superalloys
FR2628349A1 (fr) * 1988-03-09 1989-09-15 Snecma Procede de forgeage de pieces en superalliage a base de nickel
EP0969114A2 (en) * 1998-06-30 2000-01-05 Howmet Research Corporation Nickel base superalloy preweld heat treatment

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US1531445A (en) * 1920-01-13 1925-03-31 Lake Simon Making metal castings
US2304976A (en) * 1939-09-07 1942-12-15 Budd Edward G Mfg Co Spot welded sheet material
US4222794A (en) * 1979-07-02 1980-09-16 United Technologies Corporation Single crystal nickel superalloy
JPS58107292A (ja) * 1981-12-21 1983-06-25 Kawasaki Heavy Ind Ltd 管の溶接継手部処理方法及び装置
CN1012182B (zh) * 1983-12-27 1991-03-27 联合工艺公司 镍基高温合金可锻性改进
US4769087A (en) * 1986-06-02 1988-09-06 United Technologies Corporation Nickel base superalloy articles and method for making
US5106010A (en) * 1990-09-28 1992-04-21 Chromalloy Gas Turbine Corporation Welding high-strength nickel base superalloys
US5071059A (en) * 1991-03-11 1991-12-10 General Motors Corporation Method for joining single crystal turbine blade halves
FR2712307B1 (fr) * 1993-11-10 1996-09-27 United Technologies Corp Articles en super-alliage à haute résistance mécanique et à la fissuration et leur procédé de fabrication.
DE19624056A1 (de) * 1996-06-17 1997-12-18 Abb Research Ltd Nickel-Basis-Superlegierung
US5938863A (en) * 1996-12-17 1999-08-17 United Technologies Corporation Low cycle fatigue strength nickel base superalloys
US6648993B2 (en) * 2001-03-01 2003-11-18 Brush Wellman, Inc. Castings from alloys having large liquidius/solidus temperature differentials

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4574015A (en) * 1983-12-27 1986-03-04 United Technologies Corporation Nickle base superalloy articles and method for making
US4579602A (en) * 1983-12-27 1986-04-01 United Technologies Corporation Forging process for superalloys
FR2628349A1 (fr) * 1988-03-09 1989-09-15 Snecma Procede de forgeage de pieces en superalliage a base de nickel
EP0969114A2 (en) * 1998-06-30 2000-01-05 Howmet Research Corporation Nickel base superalloy preweld heat treatment

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7915566B2 (en) 2005-10-24 2011-03-29 Siemens Aktiengesellschaft Weld filler, use of the weld filler and welding process
EP1835040A1 (de) 2006-03-17 2007-09-19 Siemens Aktiengesellschaft Schweisszusatzwekstoff, Verwendung des Schweisszusatzwekstoffes, Verfahren zum Schweissen und Bauteil
EP2182084A1 (de) 2008-11-04 2010-05-05 Siemens Aktiengesellschaft Schweisszusatzwerkstoff, Verwendung des Schweisszusatzwserkstoffes und Bauteil

Also Published As

Publication number Publication date
WO2004053181A2 (de) 2004-06-24
CN1726297B (zh) 2010-05-26
US20060144477A1 (en) 2006-07-06
WO2004053181A3 (de) 2004-11-25
CN1726297A (zh) 2006-01-25
EP1570098A2 (de) 2005-09-07

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