EP3671359B1 - Herstellungsverfahren einer spiralfeder eines uhrwerks auf titanbasis - Google Patents

Herstellungsverfahren einer spiralfeder eines uhrwerks auf titanbasis Download PDF

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EP3671359B1
EP3671359B1 EP18215265.2A EP18215265A EP3671359B1 EP 3671359 B1 EP3671359 B1 EP 3671359B1 EP 18215265 A EP18215265 A EP 18215265A EP 3671359 B1 EP3671359 B1 EP 3671359B1
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EP
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Prior art keywords
deformation
manufacturing
spiral spring
heat treatment
spring according
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EP18215265.2A
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English (en)
French (fr)
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EP3671359A1 (de
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Christian Charbon
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Nivarox Far SA
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Nivarox Far SA
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Priority to EP18215265.2A priority Critical patent/EP3671359B1/de
Priority to US16/693,481 priority patent/US11650543B2/en
Priority to JP2019212905A priority patent/JP6954978B2/ja
Priority to KR1020190163654A priority patent/KR102320621B1/ko
Priority to RU2019142569A priority patent/RU2727354C1/ru
Priority to CN201911326726.3A priority patent/CN111349814B/zh
Publication of EP3671359A1 publication Critical patent/EP3671359A1/de
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    • G—PHYSICS
    • G04—HOROLOGY
    • G04B—MECHANICALLY-DRIVEN CLOCKS OR WATCHES; MECHANICAL PARTS OF CLOCKS OR WATCHES IN GENERAL; TIME PIECES USING THE POSITION OF THE SUN, MOON OR STARS
    • G04B1/00—Driving mechanisms
    • G04B1/10—Driving mechanisms with mainspring
    • G04B1/14—Mainsprings; Bridles therefor
    • G04B1/145—Composition and manufacture of the springs
    • G—PHYSICS
    • G04—HOROLOGY
    • G04B—MECHANICALLY-DRIVEN CLOCKS OR WATCHES; MECHANICAL PARTS OF CLOCKS OR WATCHES IN GENERAL; TIME PIECES USING THE POSITION OF THE SUN, MOON OR STARS
    • G04B17/00—Mechanisms for stabilising frequency
    • G04B17/04—Oscillators acting by spring tension
    • G04B17/06—Oscillators with hairsprings, e.g. balance
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, wire, rods, tubes or like semi-manufactured products by drawing
    • B21C1/02—Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
    • 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
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/02—Alloys based on vanadium, niobium, or tantalum
    • 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
    • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
    • 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
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • 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
    • G—PHYSICS
    • G04—HOROLOGY
    • G04B—MECHANICALLY-DRIVEN CLOCKS OR WATCHES; MECHANICAL PARTS OF CLOCKS OR WATCHES IN GENERAL; TIME PIECES USING THE POSITION OF THE SUN, MOON OR STARS
    • G04B17/00—Mechanisms for stabilising frequency
    • G04B17/04—Oscillators acting by spring tension
    • G04B17/06—Oscillators with hairsprings, e.g. balance
    • G04B17/066—Manufacture of the spiral spring
    • G—PHYSICS
    • G04—HOROLOGY
    • G04B—MECHANICALLY-DRIVEN CLOCKS OR WATCHES; MECHANICAL PARTS OF CLOCKS OR WATCHES IN GENERAL; TIME PIECES USING THE POSITION OF THE SUN, MOON OR STARS
    • G04B17/00—Mechanisms for stabilising frequency
    • G04B17/20—Compensation of mechanisms for stabilising frequency
    • G04B17/22—Compensation of mechanisms for stabilising frequency for the effect of variations of temperature
    • G04B17/227—Compensation of mechanisms for stabilising frequency for the effect of variations of temperature composition and manufacture of the material used

Definitions

  • the invention relates to the field of the manufacture of watch springs, in particular energy storage springs, such as barrel springs or driving or striking hairsprings, or oscillator springs, such as hairsprings.
  • the invention proposes to define and develop the appropriate manufacturing process for the manufacture of spiral clock springs.
  • the invention relates to a method of manufacturing such a clockwork spiral spring, according to independent claim 1.
  • Preferred embodiments are defined in the dependent claims.
  • the invention is aimed at the manufacture of a clockwork spiral spring with a two-phase structure.
  • the material of this spiral spring is an alloy of the titanium-based binary type, comprising niobium.
  • this alloy comprises a titanium mass proportion greater than or equal to 65.0% of the total and less than or equal to 85.0% of the total.
  • this alloy comprises a titanium mass proportion greater than or equal to 70.0% of the total and less than or equal to 85.0% of the total.
  • this alloy comprises a proportion by weight of titanium greater than or equal to 70.0% of the total and less than or equal to 75.0% of the total.
  • this alloy comprises a proportion by mass of titanium strictly greater than 76.0% of the total and less than or equal to 85.0% of the total.
  • this alloy comprises a titanium mass proportion of less than or equal to 80.0% of the total.
  • this alloy comprises a proportion by weight of titanium strictly greater than 76.0% of the total and less than or equal to 78.0% of the total.
  • this spiral spring has a two-phase microstructure comprising centered cubic beta niobium and compact hexagonal alpha titanium. More particularly, this spiral spring has a two-phase microstructure comprising a solid solution of niobium with titanium in the ⁇ phase (centered cubic structure) and a solid solution of niobium with titanium in the ⁇ phase (compact hexagonal structure), the titanium content in ⁇ phase being greater than 10% by volume.
  • the total of the proportions by mass of titanium and niobium is between 99.7% and 100% of the total.
  • the proportion by mass of oxygen is less than or equal to 0.10% of the total, or even less than or equal to 0.085% of the total.
  • the proportion by mass of tantalum is less than or equal to 0.10% of the total.
  • the proportion by mass of carbon is less than or equal to 0.04% of the total, in particular less than or equal to 0.020% of the total, or even even less than or equal to 0.0175% of the total.
  • the proportion by mass of iron is less than or equal to 0.03% of the total, in particular less than or equal to 0.025% of the total, or even even less than or equal to 0.020% of the total.
  • the mass proportion of nitrogen is less than or equal to 0.02% of the total, in particular less than or equal to 0.015% of the total, or even even less than or equal to 0.0075% of the total.
  • the proportion by mass of hydrogen is less than or equal to 0.01% of the total, in particular less than or equal to 0.0035% of the total, or even even less than or equal to 0.0005% of the total.
  • the proportion by mass of nickel is less than or equal to 0.01% of the total.
  • the mass proportion of silicon is less than or equal to 0.01% of the total.
  • the proportion by mass of nickel is less than or equal to 0.01% of the total, in particular less than or equal to 0.16% of the total.
  • the proportion by mass of ductile material or copper is less than or equal to 0.01% of the total, in particular less than or equal to 0.005% of the total.
  • the proportion by mass of aluminum is less than or equal to 0.01% of the total.
  • This spiral spring has an elastic limit greater than or equal to 1000 MPa. More particularly, the spiral spring has an elastic limit greater than or equal to 1500 MPa.
  • the spiral spring has an elastic limit greater than or equal to 2000 MPa.
  • this spiral spring has a modulus of elasticity greater than 60 GPa and less than or equal to 80 GPa.
  • the alloy thus determined allows, depending on the treatment applied during development, the manufacture of spiral springs which are spiral springs with an elastic limit greater than or equal to 1000 MPa, or barrel springs, in particular when the elastic limit greater than or equal to 1500 MPa.
  • the application to a hairspring requires properties capable of guaranteeing the maintenance of chronometric performance despite the variation in the temperatures of use of a watch incorporating such a hairspring.
  • the thermoelastic coefficient, also called CTE of the alloy is then of great importance.
  • the work-hardened beta-phase alloy has a strongly positive CTE, and the precipitation of the alpha phase, which has a strongly negative CTE, makes it possible to bring the two-phase alloy back to a CTE close to zero, which is particularly favorable.
  • a CTE of +/- 10 ppm/°C must be achieved.
  • E is the Young's modulus of the hairspring, and, in this formula, E, ⁇ and ⁇ are expressed in °C -1 .
  • CT is the thermal coefficient of the oscillator
  • (1/E. dE/dT) is the CTE of the hairspring alloy
  • ⁇ is the expansion coefficient of the balance and ⁇ that of the hairspring.
  • this alloy of coupled sequences 20 of deformation-precipitation heat treatment comprising the application of deformations (21) alternated with heat treatments (22), until obtaining a two-phase microstructure comprising a solid solution of niobium with titanium in the ⁇ phase and a solid solution of niobium with titanium in the ⁇ phase, the titanium content in the ⁇ phase being greater than 10% by volume, with an elastic limit greater than or equal to 2000 MPa.
  • the treatment cycle then comprises beforehand a beta quenching (15) to a given diameter, so that the entire structure of the alloy is beta, then a succession of these coupled sequences of deformation-precipitation heat treatment .
  • each deformation is carried out with a given deformation rate between 1 and 5, this deformation rate corresponding to the classical formula 2ln(d0/d), where d0 is the diameter of the last beta temper, and where d is the diameter of the work-hardened wire.
  • the overall accumulation of the deformations over the whole of this succession of phases leads to a total deformation rate of between 1 and 14.
  • Each sequence coupled with deformation-heat treatment of precipitation comprises, each time, a heat treatment of precipitation of the phase alpha Ti (300-700°C, 1h-30h).
  • This process variant comprising beta quenching is particularly suited to the manufacture of barrel springs. More particularly, this beta quenching is a solution treatment, with a duration of between 5 minutes and 2 hours at a temperature of between 700° C. and 1000° C., under vacuum, followed by cooling under gas.
  • this beta quenching is a solution treatment, with 1 hour at 800° C. under vacuum, followed by cooling under gas.
  • each coupled sequence of deformation-precipitation heat treatment comprises a precipitation treatment lasting between 1 hour and 80 hours at a temperature between 350° C. and 700°C. More particularly, the duration is between 1 hour and 10 hours at a temperature between 380°C and 650°C. More particularly still, the duration is from 1 hour to 12 hours, at a temperature of 380°C.
  • long heat treatments are applied, for example heat treatments carried out for a period of between 15 hours and 75 hours at a temperature of between 350° C. and 500° C. For example, heat treatments are applied for 75h to 400h at 350°C, 25h at 400°C or 18h at 480°C.
  • the method comprises between one and five, preferably three to five, coupled deformation-precipitation heat treatment sequences.
  • the first coupled deformation-precipitation heat treatment sequence comprises a first deformation with at least 30% reduction in section.
  • each coupled deformation-precipitation heat treatment sequence comprises a deformation between two precipitation heat treatments with at least 25% reduction in section.
  • a surface layer of ductile material taken from copper, nickel, cupro-nickel, cupro -manganese, gold, silver, nickel-phosphorus Ni-P and nickel-boron Ni-B, or the like, to facilitate wire forming by drawing and drawing and rolling.
  • the wire is stripped of its layer of ductile material , in particular by chemical attack, in a step 50.
  • the barrel spring it is indeed possible to carry out the manufacture by setting in ring and thermal treatment, where the setting in ring replaces the calendering.
  • the barrel spring is still generally heat-treated after ringing or after calendering.
  • a spiral spring is generally still heat treated after strapping.
  • the last phase of deformation is carried out in the form of flat rolling, and the last heat treatment is carried out on the calendered or ring-formed or strapped spring. More particularly, after drawing, the wire is rolled flat, before the manufacture of the actual spring by calendering or strapping or setting in a ring.
  • the surface layer of ductile material is deposited so as to constitute a spiral spring whose pitch is not a multiple of the thickness of the blade.
  • the surface layer of ductile material is deposited so as to form a spring whose pitch is variable.
  • ductile material or copper is thus added at a given moment to facilitate the shaping of the wire by drawing and drawing, so that a thickness of 10 to 500 micrometers remains on the wire with a final diameter of 0.3 to 1 mm.
  • the wire is stripped of its layer of ductile material or copper in particular by chemical attack, then is rolled flat before the manufacture of the actual spring.
  • ductile material or copper can be galvanic, or mechanical, it is then a shirt or a tube of ductile material or copper which is fitted on a bar of niobium-titanium alloy to a large diameter, then which is thinned during the stages of deformation of the composite bar.
  • the layer can be removed in particular by chemical attack, with a solution based on cyanides or based on acids, for example nitric acid.
  • the invention thus makes it possible in particular to produce a spiral barrel spring made of an alloy of the niobium-titanium type, typically containing more than 60% by mass of titanium.
  • a very fine lamellar bi-phase microstructure in particular nanometric, comprising a solid solution of niobium with titanium in the ⁇ phase and a solid solution of niobium with ⁇ -phase titanium, the ⁇ -phase titanium content being greater than 10% by volume.
  • This alloy combines a very high elastic limit, greater than at least 1000 MPa, or greater than 1500 MPa, or even 2000 MPa on wire, and a very low modulus of elasticity, of the order of 60 Gpa to 80 GPa. This combination of properties is well suited for a mainspring or hairspring.
  • This niobium-titanium type alloy can easily be covered with ductile material or copper, which greatly facilitates its deformation by drawing.
  • Such an alloy is known and used for the manufacture of superconductors, such as magnetic resonance imaging devices, or particle accelerators), but is not used in watchmaking. Its fine, two-phase microstructure is sought after in the case of superconductors for physical reasons and has the welcome side effect of improving the mechanical properties of the alloy.
  • Such an alloy is particularly suitable for the production of a mainspring, and also for the production of spiral springs.
  • a binary type alloy comprising niobium and titanium, of the type selected above for the implementation of the invention, is also capable of being used as a spiral wire, it has an effect similar to that of " Elinvar", with a practically zero thermo-elastic coefficient in the range of temperatures of usual use of watches, and suitable for the manufacture of self-compensating hairsprings, in particular for niobium-titanium alloys with a higher proportion by mass of titanium at 60% and up to 85%.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Mechanical Engineering (AREA)
  • General Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
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Claims (14)

  1. Verfahren zum Herstellen einer Uhrenspiralfeder, bei dem folgende Schritte nacheinander durchgeführt werden:
    - Erstellen eines Rohlings in einer Niob und Titan enthaltenden Legierung vom binären Typ, der Folgendes umfasst:
    - Niob: Rest bei 100 %;
    - einen Massenanteil von Titan, der streng größer als 60,0 % der Gesamtmenge und kleiner oder gleich 85,0 % der Gesamtmenge ist,
    - Spuren von anderen Komponenten unter O, H, C, Fe, Ta, N, Ni, Si, Cu, Al, wobei jede der Spurenkomponenten zwischen 0 und 1600 ppm der Gesamtmasse beträgt und die Summe der Spuren kleiner oder gleich 0,3 Massen-% ist;
    - Ausführen eines Behandlungszyklus, der zunächst eine Beta-Abschreckung bei einem bestimmten Durchmesser umfasst, so dass die gesamte Struktur der Legierung beta ist, dann Anwenden einer Folge von gekoppelten Abfolgen einer thermischen Verformungs-Ausfällungsbehandlung auf die Legierung, die das Anwenden von abwechselnden Verformungs-Wärmebehandlungen umfasst, bis eine zweiphasige Mikrostruktur erhalten wird, umfassend eine feste Lösung aus Niob mit Titan in der ß-Phase und eine feste Lösung aus Niob mit Titan in der α-Phase, wobei der Titangehalt in der α-Phase größer als 10 Vol.-% ist, mit einer Elastizitätsgrenze größer oder gleich 1000 MPa und einem Elastizitätsmodul größer als 60 GPa und kleiner oder gleich 80 GPa;
    - Drahtziehen, bis ein Draht mit rundem Querschnitt erhalten wird, und kompatibles Flachwalzen mit dem Eingangsabschnitt eines Kalanders oder eines Aufwindungsstifts oder dem Drehen in Ringform;
    - Kalandrieren der Spiralen im Violinschlüssel, um eine Zugfeder vor ihrem ersten Spannen zu bilden, oder Aufwinden, um eine Spiralfeder zu bilden, oder Drehen in Ringform und Wärmebehandeln für eine Zugfeder.
  2. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 1, dadurch gekennzeichnet, dass eine letzte Wärmebehandlung an der kalandrierten oder in eine Ringform gedrehten oder aufgewundenen Feder durchgeführt wird.
  3. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass das Anwenden von gekoppelten Abfolgen einer thermischen Verformungs-Ausfällungsbehandlung auf die Legierung ausgeführt wird, umfassend das Anwenden von abwechselnden Verformungs-Wärmebehandlungen, bis eine zweiphasige Mikrostruktur erhalten wird, umfassend eine feste Lösung aus Niob mit Titan in der β-Phase und eine feste Lösung aus Niob mit Titan in der α-Phase, wobei der Titangehalt in der α-Phase größer als 10 Vol.-% ist, mit einer Elastizitätsgrenze größer oder gleich 2000 MPa, wobei der Behandlungszyklus ein vorheriges Beta-Abschrecken bei einem bestimmten Durchmesser umfasst, so dass die gesamte Struktur der Legierung beta ist, dann eine Folge der gekoppelten Abfolgen einer thermischen Verformungs-Ausfällungsbehandlung, wobei jede Verformung mit einer bestimmten Verformungsrate zwischen 1 und 5 durchgeführt wird, wobei die Gesamtakkumulation der Verformungen über die gesamte Abfolge von Phasen zu einer Gesamtverformungsrate zwischen 1 und 14 führt, und das jedes Mal eine Wärmebehandlung zur Ausfällung des Ti in der Alpha-Phase umfasst.
  4. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 3, dadurch gekennzeichnet, dass das Beta-Abschrecken eine Lösungsglühbehandlung mit einer Dauer zwischen 5 Minuten und 2 Stunden bei einer Temperatur zwischen 700 °C und 1000 °C unter Vakuum ist, der eine Kühlung unter Gas folgt.
  5. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 4, dadurch gekennzeichnet, dass das Beta-Abschrecken eine Lösungsglühbehandlung von 1 Stunde bei 800 °C unter Vakuum ist, der eine Kühlung unter Gas folgt.
  6. Verfahren zum Herstellen einer Spiralfeder nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass jede gekoppelte Abfolge der thermischen Verformungs-Ausfällungsbehandlung eine Ausfällungsbehandlung mit einer Dauer zwischen 1 Stunde und 80 Stunden bei einer Temperatur zwischen 350 °C und 700 °C umfasst.
  7. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 6, dadurch gekennzeichnet, dass jede gekoppelte Abfolge der thermischen Verformungs-Ausfällungsbehandlung eine Ausfällungsbehandlung mit einer Dauer zwischen 1 Stunde und 10 Stunden bei einer Temperatur zwischen 380 °C und 650 °C umfasst.
  8. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 7, dadurch gekennzeichnet, dass jede gekoppelte Abfolge der thermischen Verformungs-Ausfällungsbehandlung eine Ausfällungsbehandlung mit einer Dauer zwischen 1 Stunde und 12 Stunden bei einer Temperatur von 450 °C umfasst.
  9. Verfahren zum Herstellen einer Spiralfeder nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass das Verfahren zwischen einer und fünf der gekoppelten Abfolgen der thermischen Verformungs-Ausfällungsbehandlung umfasst.
  10. Verfahren zum Herstellen einer Spiralfeder nach einem der Ansprüche 1 bis 9, dadurch gekennzeichnet, dass die erste gekoppelte Abfolge der thermischen Verformungs-Ausfällungsbehandlung eine erste Verformung mit mindestens 30 % Querschnittsverringerung umfasst.
  11. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 10, dadurch gekennzeichnet, dass jede der gekoppelten Abfolgen der thermischen Verformungs-Ausfällungsbehandlung, außer der ersten, eine Verformung zwischen zwei thermischen Ausfällungsbehandlungen mit mindestens 25 % Querschnittsverringerung umfasst.
  12. Verfahren zum Herstellen einer Spiralfeder nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass nach dem Erstellen des Legierungsrohlings und vor dem Drahtziehen dem Rohling eine Oberflächenschicht aus duktilem Material hinzugefügt wird, zu dem Kupfer, Nickel, Kupfernickel, Kupfermangan, Gold, Silber, Nickel-Phosphor Ni-P und Nickel-Bor Ni-B zählen, um die Formgebung des Draht durch Strecken und Drahtziehen und Walzen zu erleichtern, und dadurch, dass nach dem Drahtziehen oder nach dem Walzen oder nach einem anschließenden Vorgang des Kalandrierens oder Aufwindens oder Ringens der Draht durch Ätzen von seiner Schicht aus dem duktilen Material befreit wird.
  13. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 12, dadurch gekennzeichnet, dass der Draht nach dem Drahtziehen flachgewalzt wird, bevor die eigentliche Feder durch Kalandrieren oder Aufwinden oder Drehen in Ringform hergestellt wird.
  14. Verfahren zum Herstellen einer Spiralfeder nach Anspruch 12 oder 13, dadurch gekennzeichnet, dass die Oberflächenschicht aus duktilem Material derart aufgebracht wird, dass sie eine Feder bildet, deren Steigung konstant ist und kein Vielfaches der Klingendicke ist.
EP18215265.2A 2018-12-21 2018-12-21 Herstellungsverfahren einer spiralfeder eines uhrwerks auf titanbasis Active EP3671359B1 (de)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP18215265.2A EP3671359B1 (de) 2018-12-21 2018-12-21 Herstellungsverfahren einer spiralfeder eines uhrwerks auf titanbasis
US16/693,481 US11650543B2 (en) 2018-12-21 2019-11-25 Titanium-based spiral timepiece spring
JP2019212905A JP6954978B2 (ja) 2018-12-21 2019-11-26 チタンベースの渦巻き計時器ぜんまい
KR1020190163654A KR102320621B1 (ko) 2018-12-21 2019-12-10 티타늄 기반 나선형 타임피스 스프링
RU2019142569A RU2727354C1 (ru) 2018-12-21 2019-12-19 Спиральная часовая пружина на титановой основе
CN201911326726.3A CN111349814B (zh) 2018-12-21 2019-12-20 钛基螺旋钟表弹簧

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EP18215265.2A EP3671359B1 (de) 2018-12-21 2018-12-21 Herstellungsverfahren einer spiralfeder eines uhrwerks auf titanbasis

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EP3671359A1 EP3671359A1 (de) 2020-06-24
EP3671359B1 true EP3671359B1 (de) 2023-04-26

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EP (1) EP3671359B1 (de)
JP (1) JP6954978B2 (de)
KR (1) KR102320621B1 (de)
CN (1) CN111349814B (de)
RU (1) RU2727354C1 (de)

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Publication number Priority date Publication date Assignee Title
USD959241S1 (en) * 2020-12-21 2022-08-02 Time4Machine Inc. Spring for a construction toy
EP4060425B1 (de) * 2021-03-16 2024-10-16 Nivarox-FAR S.A. Spiralfeder für uhrwerk
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CN111349814B (zh) 2022-05-24
RU2727354C1 (ru) 2020-07-21
US20200201254A1 (en) 2020-06-25
KR20200079188A (ko) 2020-07-02
US11650543B2 (en) 2023-05-16
EP3671359A1 (de) 2020-06-24
CN111349814A (zh) 2020-06-30
JP6954978B2 (ja) 2021-10-27
JP2020101527A (ja) 2020-07-02
KR102320621B1 (ko) 2021-11-02

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