WO2005052201A2 - METHOD FOR THE PRODUCTION OF DROP FORGE PARTS CONTAINING Ti, Zr, Hf - Google Patents

METHOD FOR THE PRODUCTION OF DROP FORGE PARTS CONTAINING Ti, Zr, Hf Download PDF

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Publication number
WO2005052201A2
WO2005052201A2 PCT/EP2004/012952 EP2004012952W WO2005052201A2 WO 2005052201 A2 WO2005052201 A2 WO 2005052201A2 EP 2004012952 W EP2004012952 W EP 2004012952W WO 2005052201 A2 WO2005052201 A2 WO 2005052201A2
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Prior art keywords
drop
weight
titanium
elasticity
modulus
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PCT/EP2004/012952
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German (de)
French (fr)
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WO2005052201A3 (en
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Andreas Barth
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Daimlerchrysler Ag
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Priority to JP2006540282A priority Critical patent/JP2007512433A/en
Priority to US10/580,896 priority patent/US20070068608A1/en
Publication of WO2005052201A2 publication Critical patent/WO2005052201A2/en
Publication of WO2005052201A3 publication Critical patent/WO2005052201A3/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C16/00—Alloys based on zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/186—High-melting or refractory metals or alloys based thereon of zirconium or alloys based thereon

Definitions

  • the invention relates to a process for the production of drop forgings which essentially consist of titanium, zirconium hafnium or a corresponding alloy.
  • the invention also relates to such drop forgings.
  • Titanium in particular is an interesting light metal because it is almost 50% lighter than steel. Therefore, Ti, Zr, Hf components are particularly interesting in the motor vehicle sector if unsprung or rotating or oscillating masses are to be reduced.
  • drop-forged parts made of bars, wires
  • forged connecting rods, crankshafts and camshafts, or valve parts should be mentioned.
  • titanium has a comparatively low modulus of elasticity (in short: modulus of elasticity in GPa; Materials Properties Handbook: Titanium Alloys, Editors: Boyer, Welsch, Collings, ASM International, Materials Park, OH 44073-002) ,
  • the modulus of elasticity of titanium alloys is only approx. 90 GPa, of steel approx. 210 GPa, of Al alloys approx. 70 GPa and of Mg alloys approx. 30 to 40 GPa.
  • Drop forgings of titanium moving parts in engines can therefore only withstand low loads.
  • DE 36 15 425 relates to a complex plasma coating process using titanium alloys on machine elements for hardening them.
  • the object is achieved by a process in which materials or alloys containing 80% by weight or more of Ti and / or Zr and / or Hf, in or during the shaping, above 5-15 K of the a / ⁇ - Phase boundary heated and then cooled. Heating is preferably to be provided for about 20 to 60 minutes. This ensures that the modulus of elasticity and strength of the Ti, Zr, Hf materials used in and during the production of the drop forged part is increased.
  • Suitable Ti, Zr, Hf materials according to the invention are titanium as such, zirconium as such, hafnium as such; however, preferably alloys containing Ti and / or Zr and / or Hf to 80 wt.% or more, preferably 90 wt.%, but particularly preferred are titanium alloys with a proportion of 80 wt.% titanium, preferably 90 wt.% titanium , Zr and Hf can be contained as additional minor components in the order of 1 to 20% by weight, preferably 5 to 15% by weight.
  • Mixtures of conventional metals can also be present, such as Al, Si, Mg, Fe, Ni, Co, Mo, V or other light and heavy metals.
  • Other preferred alloys are Ti Al 6 V 4 or Ti Al 6 Fe 2 Si, such as those used in motor vehicles.
  • ⁇ // 3-Ti alloys or materials containing ci / ⁇ -Tl which have both high-strength, cubic, body-centered 3-phase and also hexagonal ⁇ -phase with a high modulus of elasticity. More / 3-phases are formed in so-called high-temperature forming and more ⁇ -phases in low-temperature forming.
  • reshaping is carried out in the / ⁇ region, specifically when heating 5-15 ° C., preferably 8-10-12 ° C. above the a / ⁇ phase boundary.
  • ⁇ -Ti changes into ⁇ -T ⁇ (so-called ci / ⁇ phase boundary), i.e.
  • the heating should take place at 887-897 ° C.
  • the corresponding preferred heating value is 975 ° C ⁇ 15 ° C.
  • the heating time in said temperature range is at least 20 minutes to 45 minutes or longer, but preferably not longer than 1 hour.
  • FIG. 1 shows an a / ⁇ weave structure or a composite material according to the invention.
  • This temperature-dependent deformation area is to be selected very narrowly, or heating or forming temperatures of ⁇ 15 K, preferably ⁇ 5 K, are to be set in order to achieve the optimum forming range of 10 K above the a / ⁇ phase limit. If this area is left, there are either isolated a- or 3-phases in a ß- or ⁇ -basic matrix (FIG.
  • the desired o * // 3 weave structure can be improved with regard to greater interweaving of the a and phases by slowly cooling in air or in a gas atmosphere after the shaping.
  • the a / ß-eb structure is further penetrated by the ⁇ phase.
  • an alternating arrangement of the cü phase and the ß phase in the material is achieved.
  • a mixed phase is obtained in an ⁇ / web structure.
  • Figure 1 a / ß weave structure (weave structure) of a Ti connecting rod forged at 975 ° C made of Ti AI 6 Fe2 Si (white a and gray jS lamellae).
  • Figure 2 a / ß weave structure (weave structure) of a Ti connecting rod forged at 990 ° C made of Ti Al 6 Fe 2 Si with isolated white a islands.
  • Optimal a / ß weave structure (weave structure) of a Ti connecting rod made of Ti AI 6 Fe2 Si (white a- and gray ß-lamellas) and then stress relieved at 650 ° C.

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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)
  • Forging (AREA)
  • Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

The invention relates to a method for the production of drop forge parts essentially comprising titanium, zirconium, hafnium or a corresponding alloy, enabling the rigidity thereof to be increased.

Description

Verfahren zur Herstellung von Ti, Zr, Hf enthaltenden Gesenkschmiedeteilen Process for the production of drop forgings containing Ti, Zr, Hf
Die Erfindung betrifft ein Verfahren zur Herstellung von Gesenkschmiedeteilen, die im wesentlichen aus Titan, Zirkonium Hafnium oder einer entsprechenden Legierung bestehen. Die Erfindung betrifft außerdem derartige Gesenkschmiedeteile.The invention relates to a process for the production of drop forgings which essentially consist of titanium, zirconium hafnium or a corresponding alloy. The invention also relates to such drop forgings.
Insbesondere Titan ist ein interessantes Leichtmetall, da es fast 50 % leichter ist als Stahl. Daher sind Ti, Zr, Hf - Bauteile im Kraftfahrzeugbereich besonders interessant , wenn ungefederte oder rotierende bzw. oszillierende Massen reduziert werden sollen. In diesem Zusammenhang sind Gesenkschmiedeteile (aus Stäben, Drähten) , insbesondere geschmiedete Pleuel, Kurbel- und Nockenwellen oder Ventilteile zu nennen. Titan verfügt im Vergleich zu metallischen Werkstoffen jedoch über ein vergleichsweise niedriges Elastizitätsmodul (kurz: E-Modul in GPa; Materials Properties Handbook: Titani- um Alloys, Editors: Boyer, Welsch, Collings, ASM International , Materials Park, OH 44073-002) . So beträgt das E-Modul von Titan-Legierungen lediglich ca. 90 GPa, von Stahl ca. 210 GPa, von AI-Legierungen ca. 70 GPa und von Mg-Legierungen ca. 30 bis 40 GPa.Titanium in particular is an interesting light metal because it is almost 50% lighter than steel. Therefore, Ti, Zr, Hf components are particularly interesting in the motor vehicle sector if unsprung or rotating or oscillating masses are to be reduced. In this context, drop-forged parts (made of bars, wires), in particular forged connecting rods, crankshafts and camshafts, or valve parts should be mentioned. However, compared to metallic materials, titanium has a comparatively low modulus of elasticity (in short: modulus of elasticity in GPa; Materials Properties Handbook: Titanium Alloys, Editors: Boyer, Welsch, Collings, ASM International, Materials Park, OH 44073-002) , The modulus of elasticity of titanium alloys is only approx. 90 GPa, of steel approx. 210 GPa, of Al alloys approx. 70 GPa and of Mg alloys approx. 30 to 40 GPa.
Gesenkschmiedeteile von sich in Motoren bewegenden Bauteilen aus Titan, wie beispielsweise Pleuels, Kurbelwellen, Nocken- wellen und/oder Ventilteilen, können folglich nur geringen Belastungen standhalten.Drop forgings of titanium moving parts in engines, such as connecting rods, crankshafts, cam shafts and / or valve parts can therefore only withstand low loads.
Im Stand der Technik sind Beschichtungsver ahren für Bauelemente beschrieben, die zu einer Härtung der Titanlegierung führen. DE 36 15 425 betrifft ein aufwändiges Plasmabeschich- tungsverfahren mittels Titanlegierungen auf Maschinenelementen zu deren Härtung.The prior art describes coating processes for components which lead to hardening of the titanium alloy. DE 36 15 425 relates to a complex plasma coating process using titanium alloys on machine elements for hardening them.
Es ist Aufgabe der vorliegenden Erfindung ein Verfahren zur Herstellung von Gesenkschmiedeteilen, die im wesentlichen aus Ti, Zr, Hf oder einer entsprechenden Legierung bestehen, bereitzustellen, bei welchem ein hoher E-Modul der Gesenkschmiedeteile erzielt wird.It is the object of the present invention to provide a method for producing drop forgings which essentially consist of Ti, Zr, Hf or a corresponding alloy, in which a high modulus of elasticity of the drop forgings is achieved.
Die Aufgabe wird durch ein Verfahren gelöst, bei dem zu 80 Gew. % oder mehr Ti und/oder Zr und/oder Hf enthaltende Materialien, oder Legierungen davon, in oder während des Umfor- mens oberhalb 5- 15 K der a/ß- Phasengrenze erwärmt und anschließend abgekühlt werden. Vorzugsweise ist eine Erwärmung für ca. 20 bis 60 Minuten vorzusehen. Dadurch wird erreicht, dass das E-Modul und Festigkeit der verwendeten Ti, Zr, Hf - Materialien in und während der Herstellung des Gesenkschmiedeteils erhöht wird.The object is achieved by a process in which materials or alloys containing 80% by weight or more of Ti and / or Zr and / or Hf, in or during the shaping, above 5-15 K of the a / β- Phase boundary heated and then cooled. Heating is preferably to be provided for about 20 to 60 minutes. This ensures that the modulus of elasticity and strength of the Ti, Zr, Hf materials used in and during the production of the drop forged part is increased.
Mit Hilfe des erfindungsgemäßen Verfahrens können im Vergleich zu Stahlbauteilen bis zu 35 % oder mehr der oszillierenden Massen in einem Motor, insbesondere bei Pleuel, Kurbel- und Nockenwellen und/oder Ventilteilen, reduziert werden. Vorteile ergeben sich hinsichtlich verbesserter Motordynamik, geringerer Geräuschemission, Entfall der Lancester - Ausgleichswelle sowie Kraftstoffeinsparung . Als Ti, Zr, Hf - Materialien sind erfindungsgemäß geeignet Titan als solches, Zirconium als solches, Hafnium als solches; bevorzugt jedoch Legierungen enthaltend Ti und/oder Zr und/oder Hf zu 80 Gew. % oder mehr, vorzugsweise 90 Gew. %, Besonders bevorzugt sind jedoch Titan - Legierungen mit einem Anteil an 80 Gew. % Titan, vorzugsweise 90 Gew. % Titan. Zr und Hf können als weitere Nebenbestandteile in der Größenordnung 1 - 20 Gew. %, vorzugsweise 5 -15 Gew. % enthalten sein. Ebenfalls können Beimengungen üblicher Metalle enthalten sein, wie AI, Si, Mg, Fe, Ni, Co, Mo, V oder andere Leicht- und Schwermetalle . Weitere bevorzugte Legierungen sind Ti AI 6 V 4 oder Ti AI 6 Fe 2 Si, wie sie im Kraftfahrzeugb u zum Einsatz kommen.With the aid of the method according to the invention, up to 35% or more of the oscillating masses in an engine can be reduced in comparison to steel components, in particular in the case of connecting rods, crankshafts and camshafts and / or valve parts. There are advantages in terms of improved engine dynamics, lower noise emissions, elimination of the Lancester balancer shaft and fuel savings. Suitable Ti, Zr, Hf materials according to the invention are titanium as such, zirconium as such, hafnium as such; however, preferably alloys containing Ti and / or Zr and / or Hf to 80 wt.% or more, preferably 90 wt.%, but particularly preferred are titanium alloys with a proportion of 80 wt.% titanium, preferably 90 wt.% titanium , Zr and Hf can be contained as additional minor components in the order of 1 to 20% by weight, preferably 5 to 15% by weight. Mixtures of conventional metals can also be present, such as Al, Si, Mg, Fe, Ni, Co, Mo, V or other light and heavy metals. Other preferred alloys are Ti Al 6 V 4 or Ti Al 6 Fe 2 Si, such as those used in motor vehicles.
Erfindungsgemäß werden α//3-Ti-Legierungen bzw. ci/ß-Tl enthaltende Materialien, die sowohl an hochfester, kubisch, raumzentrierter 3-Phase als auch an hexagonaler α-Phase mit hohem E-Modul verfügen, verwendet. Beim so genannten Hochtempera- turumformen werden mehr /3-Phasen und beim Niedrigterαperatur- umformen mehr α-Phasen gebildet. Erfindungsgemäß wird im /ß- Gebiet umgeformt und zwar beim Erwärmen 5-15°C vorzugsweise 8 - 10 - 12°C oberhalb der a/ ß-Phasengrenze . Bei reinem Titan geht beispielsweise bei 882, 5°C α-Ti in ß-T± über (so genannte ci/ß-Phasengrenze) , d.h. die Erwärmung sollte erfindungsgemäß bei 887 - 897 °C erfolgen. Für Ti AI 6 V 4 oder T± AI 6 Fe 2 Si liegt der entsprechende bevorzugte Erwärmungswert bei 975°C ±15°C.According to the invention, α // 3-Ti alloys or materials containing ci / β-Tl are used which have both high-strength, cubic, body-centered 3-phase and also hexagonal α-phase with a high modulus of elasticity. More / 3-phases are formed in so-called high-temperature forming and more α-phases in low-temperature forming. According to the invention, reshaping is carried out in the / β region, specifically when heating 5-15 ° C., preferably 8-10-12 ° C. above the a / β phase boundary. In the case of pure titanium, for example, at 882.5 ° C., α-Ti changes into β-T ± (so-called ci / β phase boundary), i.e. According to the invention, the heating should take place at 887-897 ° C. For Ti AI 6 V 4 or T ± AI 6 Fe 2 Si, the corresponding preferred heating value is 975 ° C ± 15 ° C.
Die Erwärmungsdauer im besagten Temperaturbereich beträgt mindestens 20 Minuten bis 45 Minuten oder länger, vorzugsweise jedoch nicht länger als 1 Stunde.The heating time in said temperature range is at least 20 minutes to 45 minutes or longer, but preferably not longer than 1 hour.
Hierdurch wird beim Aufwärmen die α-Niedrigtemperatixrphase durch die ß-Hochtemperaturphase derart durchsetzt, dass sich eine a/ß-WebStruktur bzw. ein erfindungsgemäßer Verbundwerkstoff ergibt (Figur 1) , der die hohen Festigkeitseigenschaften der /3-Phase sowie den höheren E-Modul der α-Phase erfindungsgemäß vereinigt . Dieses te peraturabhängige ümformgebiet ist sehr eng auszuwählen, bzw. es sind Erwärmungs- bzw. Umformtemperaturen von ±15 K, vorzugsweise ±5 K um den optimalen Umformbereich von 10 K oberhalb der a/ß-Phasengrenze einzustellen. Wird dieser Bereich verlassen, so liegen entweder isolierte a- oder 3-Phasen in einer ß- bzw. α-Grundmatrix vor (Figur 2) , so dass nachteilig der niedrige E-Modul der ß- Phase resultiert. Die gewünschte o*//3-Webstruktur lässt sich erfindungsgemäß hinsichtlich einer stärkeren Durchflechtung der a- und -Phasen verbessern, indem nach dem Umformen langsam an Luft bzw. in Gasatmosphäre abgekühlt wird. Hierdurch wird die a/ß- ebStruktur weiter durch die α-Phase durchsetzt. Im Ergebnis wird eine alternierende Anordnung der cü-Phase und der ß-Phase im Material erreicht. Im weitesten Sinne wird eine Mischphase in einer α/ -Webstruktur erhalten. Erfindungsgemäß kann sich nach 'dem Umformen ein Entspannungsglühen bei 650 ± 50°C anschließen, um neben dem Abbau ungewünschter Umformeigenspannungen eine stärkere Durchsetzung der a/ ß- Webstruktur mit der α-Phase mit hohem E-Modul zu erzielenAs a result, when warming up, the α-low temperature phase is penetrated by the β-high temperature phase in such a way that an a / β weave structure or a composite material according to the invention results (FIG. 1), which combines the high strength properties of the / 3 phase and the higher modulus of elasticity of the α phase according to the invention. This temperature-dependent deformation area is to be selected very narrowly, or heating or forming temperatures of ± 15 K, preferably ± 5 K, are to be set in order to achieve the optimum forming range of 10 K above the a / β phase limit. If this area is left, there are either isolated a- or 3-phases in a ß- or α-basic matrix (FIG. 2), so that the low modulus of elasticity of the ß-phase results disadvantageously. According to the invention, the desired o * // 3 weave structure can be improved with regard to greater interweaving of the a and phases by slowly cooling in air or in a gas atmosphere after the shaping. As a result, the a / ß-eb structure is further penetrated by the α phase. As a result, an alternating arrangement of the cü phase and the ß phase in the material is achieved. In the broadest sense, a mixed phase is obtained in an α / web structure. According to the invention according 'to forming a stress relief anneal at 650 ± 50 ° C connect to achieve in addition to the reduction of undesired Umformeigenspannungen a stronger enforcement of a / SS weave structure of the α-phase having a high modulus of elasticity
(Figur 3) . Hierbei ist die Glühzeit derart zu begrenzen, das die c,//3-Webstruktur nicht zerstört wird. Anhand bei 975°C ± 5°C gesenkgeschmiedeter Ti-Pleueln, die nach dem Umformen langsam in Luft abkühlten, konnte bei den a/ß-Legierungen Ti AI 6 V 4 ein E-Modul von 130 GPa bzw. Ti AI 6 Fe 2 Si ein E- Modul von 140 GPa realisiert werden. Ein anschließendes Entspannungsarmglühen bei 650°C erbringt eine zusätzliche E- ModulSteigerung von mindestens 5 GPa. Die durch das erfindungsgemäße Verfahren erzielte Zugfestigkeit liegt bei Legierungen (z.B. Ti AI 6 V 4, Ti AI 6 Fe 2 Si) oberhalb 1100 MPa bzw. die Dehngrenze oberhalb 1000 MPa. Dies entspricht den Festigkeitswerten hochfester /3-Ti-Legierun-gen, die oberhalb denen von Stahl liegen. So konnte vorteilhaft die oszillierende Masse bei Ti AI 6 Fe 2 Si- Pleueln im Vergleich zu hochfesten Stahlpleueln bis zu 35% - 45 % reduziert werden.(Figure 3). The glow time must be limited in such a way that the c, // 3 weave structure is not destroyed. On the basis of drop-forged Ti connecting rods at 975 ° C ± 5 ° C, which slowly cooled in air after forming, an elastic modulus of 130 GPa or Ti AI 6 Fe 2 could be achieved for the a / ß alloys Ti AI 6 V 4 An E-module of 140 GPa can be realized. Subsequent stress relief annealing at 650 ° C results in an additional increase in modulus of elasticity of at least 5 GPa. The tensile strength achieved by the method according to the invention is in alloys (for example Ti Al 6 V 4, Ti Al 6 Fe 2 Si) above 1100 MPa or the yield strength above 1000 MPa. This corresponds to the strength values of high-strength / 3-Ti alloys above those of steel. In this way, the oscillating mass of Ti AI 6 Fe 2 Si connecting rods could advantageously be reduced by up to 35% - 45% compared to high-strength steel connecting rods.
Beschreibung der Figuren:Description of the figures:
Figur 1 : a / ß- Webgefüge (Webstruktur) eines bei 975 °C geschmiedeten Ti-Pleuels aus Ti AI 6 Fe2 Si (weiße a- und graue jS- Lamellen) .Figure 1: a / ß weave structure (weave structure) of a Ti connecting rod forged at 975 ° C made of Ti AI 6 Fe2 Si (white a and gray jS lamellae).
Figur 2 : a / ß- Webgefüge (Webstruktur) eines bei 990 °C geschmiedeten Ti-Pleuels aus Ti AI 6 Fe 2 Si mit isolierten weißen a- Inseln.Figure 2: a / ß weave structure (weave structure) of a Ti connecting rod forged at 990 ° C made of Ti Al 6 Fe 2 Si with isolated white a islands.
Figur 3 :Figure 3:
Optimales a / ß- Webgefüge (Webstruktur) eines bei 975 °C umgeformten und dann bei 650 °C spannungsarmgeglüht en Ti- Pleuels aus Ti AI 6 Fe2 Si (weiße a- und graue ß- Lamellen) . Optimal a / ß weave structure (weave structure) of a Ti connecting rod made of Ti AI 6 Fe2 Si (white a- and gray ß-lamellas) and then stress relieved at 650 ° C.

Claims

Patentansprüche claims
1. Verfahren zum Herstellen von Gesenkschmiedeteilen, insbesondere von sich in Motoren bewegenden Gesenkschmiedeteilen wie Pleuels, Kurbelwellen, Nockenwellen und/oder Ven- . tilteilen, aus zu 80 Gew. % oder mehr Ti und/oder Zr und/oder Hf enthaltendem Material , wobei das Gesenkschmiedeteil beim Umformen auf 5 — 15 K oberhalb der a/ß - Phasengrenze erwärmt und anschließend abgekühlt wird.1. Method for producing drop forgings, in particular drop forgings moving in engines such as connecting rods, crankshafts, camshafts and / or Ven. parts, made of material containing 80% by weight or more of Ti and / or Zr and / or Hf, the drop forged part being heated to 5-15 K above the a / β phase boundary and then cooled.
2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass das Material für ca. 20 bis 60 Minuten erwärmt wird.2. The method according to claim 1, characterized in that the material is heated for about 20 to 60 minutes.
3. Verfahren nach Anspruch 1 oder 2 , dadurch gekennzeichnet , dass ein Entspannungsglühen bei 6O0 - 700 °C nach dem Abkühlen erfolgt.3. The method according to claim 1 or 2, characterized in that a relaxation annealing is carried out at 6O0 - 700 ° C after cooling.
4. Verfahren nach Anspruch 1 , 2 oder 3 , dadurch gekennzeichnet, dass das E-Modul und die Festigkeit in der Ti und/oder und/oder Zr und/oder Hf enthaltende Materialien, oder Legierungen davon, erhöht wird.4. The method according to claim 1, 2 or 3, characterized in that the modulus of elasticity and the strength in the Ti and / or and / or Zr and / or Hf-containing materials, or alloys thereof, is increased.
5. Verfahren nach einem der Ansprüche 1 bis 4 , dadurch gekennzeichnet , dass eine Titan-Legierung 1- 20 Gew. % oder 5- 15 Gew. % Zr und/oder Hf und ggf. Beimengungen anderer Leicht - o- der Schwermetalle enthält.5. The method according to any one of claims 1 to 4, characterized in that a titanium alloy contains 1-20% by weight or 5-15% by weight of Zr and / or Hf and, if necessary, admixtures of other light or heavy metals.
6. Verfahren nach Anspruch 1 , 2 oder 3 , dadurch gekennzeichnet, dass eine Titan-Legierung 90 Gew. % Titan enthält oder ausgewählt ist aus Ti AI 6 V 4 oder Ti AI 6 Fe2 Si .6. The method according to claim 1, 2 or 3, characterized in that a titanium alloy contains 90% by weight of titanium or is selected from Ti AI 6 V 4 or Ti AI 6 Fe2 Si.
7. Verfahren nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass ein a/ß - Webgefüge oder Verbundwerkstoff ausgebildet wird.7. The method according to any one of claims 1 to 6, characterized in that an a / ß - woven structure or composite material is formed.
8. Verfahren nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass das Gesenkschmiedeteil nach dem Schmieden langsam an Luft abgekühlt wird.8. The method according to any one of claims 1 to 7, characterized in that the drop forging is slowly cooled in air after forging.
9. Gesenkschmiedeteil, insbesondere Pleuel, Kurbelwelle, Nockenwelle und/oder Ventilteil, erhältlich aus einem Verfahren gemäß den Ansprüchen 1 bis 8.9. drop forged part, in particular connecting rod, crankshaft, camshaft and / or valve part, obtainable from a process according to claims 1 to 8.
10. Gesenkschmiedeteil, insbesondere Pleuel, Kurbelwelle, Nockenwelle und/oder Ventilteil, aus zu 80 Gew. % oder mehr Ti und/oder Zr und/oder Hf enthaltendem Material, oder einer Legierung davon, bei dem während des Umformens das Material auf 5- 15 K oberhalb der a/ß - Phasengrenze derart erwärmt und anschließend derart abgekühlt worden ist, dass ein erhöhter E-Modul vorliegt. 10. Drop-forged part, in particular connecting rod, crankshaft, camshaft and / or valve part, made of material containing 80% by weight or more of Ti and / or Zr and / or Hf, or an alloy thereof, in which the material is reduced to 5- 15 K above the a / ß phase boundary has been heated and then cooled in such a way that an increased modulus of elasticity is present.
PCT/EP2004/012952 2003-11-29 2004-11-16 METHOD FOR THE PRODUCTION OF DROP FORGE PARTS CONTAINING Ti, Zr, Hf WO2005052201A2 (en)

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WO2005052201A3 (en) 2006-02-09
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US20070068608A1 (en) 2007-03-29

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