EP3796101A1 - Spiralfeder für uhrwerk - Google Patents

Spiralfeder für uhrwerk Download PDF

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Publication number
EP3796101A1
EP3796101A1 EP19198759.3A EP19198759A EP3796101A1 EP 3796101 A1 EP3796101 A1 EP 3796101A1 EP 19198759 A EP19198759 A EP 19198759A EP 3796101 A1 EP3796101 A1 EP 3796101A1
Authority
EP
European Patent Office
Prior art keywords
spiral spring
deformation
titanium
weight
manufacturing
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.)
Pending
Application number
EP19198759.3A
Other languages
English (en)
French (fr)
Inventor
Christian Charbon
Marco Verardo
Lionel MICHELET
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.)
Nivarox Far SA
Nivarox SA
Original Assignee
Nivarox Far SA
Nivarox SA
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 Nivarox Far SA, Nivarox SA filed Critical Nivarox Far SA
Priority to EP19198759.3A priority Critical patent/EP3796101A1/de
Priority to US16/936,682 priority patent/US20210088971A1/en
Priority to JP2020136578A priority patent/JP7148577B2/ja
Priority to CN202010985588.6A priority patent/CN112538587B/zh
Priority to CN202210710467.XA priority patent/CN114990402A/zh
Publication of EP3796101A1 publication Critical patent/EP3796101A1/de
Pending legal-status Critical Current

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Classifications

    • 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
    • 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
    • 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
    • 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
    • G04B17/063—Balance construction

Definitions

  • the invention relates to a spiral spring intended to equip a balance of a clockwork movement. It also relates to the method of manufacturing this spiral spring.
  • the invention proposes to define a new type of clockwork spiral spring, based on the selection of a particular material, and to develop the appropriate manufacturing process.
  • the invention relates to a clockwork spiral spring made from an alloy of niobium and titanium.
  • the titanium content is between 1% (limit included) and 40% (limit not included) by weight.
  • it is between 5 and 35% by weight (limits included), preferably between 15 and 35% (limits included) and more preferably between 27 and 33% (limits included).
  • the remainder consists of niobium and impurities including interstitials such as H, C, N and / or O, the percentage of impurities being less than or equal to 0.3% by weight.
  • the invention also relates to the method of manufacturing this clockwork spiral spring as claimed in the appendix.
  • the invention relates to a clockwork spiral spring made from a binary type alloy comprising niobium and titanium.
  • the percentage by weight 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 percentage by weight of tantalum is less than or equal to 0.10% of the total.
  • the percentage by weight 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 less than or equal to 0.0175% of the total.
  • the percentage by weight 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 less than or equal to 0.020% of the total.
  • the percentage by weight 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 less than or equal to 0.0075% of the total.
  • the percentage by weight 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 less than or equal to 0.0005% of the total.
  • the percentage by weight of nickel is less than or equal to 0.01% of the total.
  • the percentage by weight of silicon is less than or equal to 0.01% of the total.
  • the percentage by weight 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 percentage by weight of 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 percentage by weight of aluminum is less than or equal to 0.01% of the total.
  • this spiral spring has a two-phase microstructure comprising niobium in the centered cubic beta phase and titanium in the compact hexagonal alpha phase.
  • thermoelastic coefficient also called CTE of the alloy
  • CTE the thermoelastic coefficient
  • dM dT 1 2 E of dT - ⁇ + 3 2 ⁇ ⁇ 86400 s j ° C
  • M and T are respectively the rate and the temperature.
  • E is the Young's modulus of the spiral spring, and, in this formula, E, ⁇ and ⁇ are expressed in ° C -1 .
  • CT is the thermal coefficient of the oscillator, (1 / E.
  • DE / dT DE / dT
  • ⁇ is the expansion coefficient of the balance and ⁇ that of the balance spring.
  • the hardened beta-phase alloy exhibits 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 to a CTE close to zero, which is particularly favorable.
  • too high a percentage of titanium leads to the formation of brittle phases.
  • a percentage of titanium less than 40% by weight makes it possible to obtain a good compromise between the various desired properties.
  • the interaction between dislocations and C, H, N, O interstitials present in the alloy as well as the interaction between dislocations and alpha titanium precipitates also play a favorable role on CTE. .
  • the setting in motion of the dislocations as a function of the temperature causes a reduction in the Young's modulus of the spiral spring which counteracts the positive anomaly of the beta phase.
  • the spiral spring produced with this alloy has an elastic limit greater than or equal to 500 MPa and more precisely between 500 and 1000 MPa.
  • it has a modulus of elasticity less than or equal to 120 GPa and preferably less than or equal to 110 GPa.
  • each strain is performed with a given strain rate between 1 and 5, this strain rate corresponding to the classic formula 2ln (d0 / d), where d0 is the diameter of the last beta hardening, and where d is the diameter of the hardened wire.
  • the global accumulation of the deformations over the whole of this succession of sequences brings a total rate of deformation of between 1 and 14.
  • Each coupled sequence of deformation-heat treatment comprises, each time, a heat treatment of precipitation of the alpha Ti phase. .
  • Beta quenching prior to the deformation and heat treatment sequences is a solution treatment, with a duration of between 5 minutes and 2 hours at a temperature between 700 ° C and 1000 ° C, under vacuum, followed by a gas cooling.
  • this beta quenching is a solution treatment, for 1 hour at 800 ° C. under vacuum, followed by cooling under gas.
  • the heat treatment is a precipitation treatment lasting between 1 hour and 200 hours at a temperature between 300 ° C and 700 ° C. More particularly, the duration is between 5 hours and 30 hours at a temperature between 400 ° C and 600 ° C.
  • the method comprises between one and five coupled sequences of deformation-heat treatment.
  • the first coupled strain-heat treatment sequence comprises a first strain with at least 30% reduction in section.
  • each coupled sequence of heat-treatment-strain comprises a strain between two heat treatments with at least 25% reduction in section.
  • a surface layer of ductile material is added to the blank, taken from among copper, nickel, cupro- nickel, cupro-magnanese, gold, silver, nickel-phosphorus Ni-P and nickel-boron Ni-B, or the like, to facilitate forming into a wire shape during deformation.
  • the wire is freed from its layer of ductile material, in particular by chemical attack.
  • the surface layer of ductile material is deposited so as to constitute a spiral spring, the pitch of which is not a multiple of the thickness of the blade.
  • the surface layer of ductile material is deposited so as to constitute a spring whose pitch is variable.
  • ductile material or copper is thus added at a given moment to facilitate the shaping in the form of wire, so that a thickness of 10 to 500 micrometers remains on the wire. with a final diameter of 0.3 to 1 millimeters.
  • the wire is stripped of its layer of ductile or copper material in particular by chemical attack, then is rolled flat before the manufacture of the spring proper by slipping.
  • the supply of ductile or copper material can be galvanic, or else mechanical, it is then a jacket or a tube of ductile or copper material. which is fitted to a large diameter niobium-titanium alloy bar, and then which is thinned during the deformation steps of the composite bar.
  • a diffusion barrier layer for example nb, can be added between the nb-Ti and the Cu in order to avoid the formation of intermetallics which are harmful to the deformability of the material.
  • the thickness of this layer is chosen so as to correspond to a thickness of 100 nm to 1 ⁇ m on the wire with a diameter of 0.1 mm.
  • the layer can be removed in particular by chemical attack, with a solution based on cyanides or based on acids, for example nitric acid.
  • a very fine two-phase lamellar microstructure in particular nanometric, comprising or composed of beta niobium and alpha titanium.
  • This alloy combines a very high elastic limit, greater than at least 500 MPa, and a very low modulus of elasticity, of the order of 80 GPa to 120 GPa. This combination of properties works well for a spiral spring.
  • the alloy after the deformation-heat treatment sequences exhibits a ⁇ 110> texture.
  • this niobium-titanium alloy according to the invention can easily be covered with ductile material or copper, which greatly facilitates its deformation by drawing.
  • a binary type alloy comprising niobium and titanium, of the type selected above for the implementation of the invention, also exhibits an effect similar to that of "Elinvar", with a thermoelastic coefficient practically zero. within the temperature range of usual use of watches, and suitable for the manufacture of self-compensating balance springs.

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  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Engineering & Computer Science (AREA)
  • General Physics & Mathematics (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Springs (AREA)
  • Conductive Materials (AREA)
EP19198759.3A 2019-09-20 2019-09-20 Spiralfeder für uhrwerk Pending EP3796101A1 (de)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP19198759.3A EP3796101A1 (de) 2019-09-20 2019-09-20 Spiralfeder für uhrwerk
US16/936,682 US20210088971A1 (en) 2019-09-20 2020-07-23 Balance spring for a horological movement
JP2020136578A JP7148577B2 (ja) 2019-09-20 2020-08-13 計時器用ムーブメントのためのバランスばね
CN202010985588.6A CN112538587B (zh) 2019-09-20 2020-09-18 用于钟表机芯的摆轮游丝
CN202210710467.XA CN114990402A (zh) 2019-09-20 2020-09-18 用于钟表机芯的摆轮游丝

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP19198759.3A EP3796101A1 (de) 2019-09-20 2019-09-20 Spiralfeder für uhrwerk

Publications (1)

Publication Number Publication Date
EP3796101A1 true EP3796101A1 (de) 2021-03-24

Family

ID=67998402

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19198759.3A Pending EP3796101A1 (de) 2019-09-20 2019-09-20 Spiralfeder für uhrwerk

Country Status (4)

Country Link
US (1) US20210088971A1 (de)
EP (1) EP3796101A1 (de)
JP (1) JP7148577B2 (de)
CN (2) CN114990402A (de)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3502289B1 (de) * 2017-12-21 2022-11-09 Nivarox-FAR S.A. Herstellungsverfahren einer spiralfeder für uhrwerk
EP4123393A1 (de) 2021-07-23 2023-01-25 Nivarox-FAR S.A. Spiralfeder für uhrwerk

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070133355A1 (en) * 2003-11-07 2007-06-14 Seik Epson Corporation Timepiece and spring thereof
CN107710081A (zh) * 2015-06-03 2018-02-16 Eta瑞士钟表制造股份有限公司 经由快慢针组件精细调节的谐振器

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ES2171872T3 (es) * 1997-06-20 2002-09-16 Rolex Montres Espiral autocompensadora para oscilador mecanico de balancin-espiral para dispositivo de movimiento de relojeria y procedimiento de fabricacion de la espiral.
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US6767418B1 (en) * 1999-04-23 2004-07-27 Terumo Kabushiki Kaisha Ti-Zr type alloy and medical appliance formed thereof
EP1258786B1 (de) * 2001-05-18 2008-02-20 Rolex Sa Selbstkompensierende Feder für einen mechanischen Oszillator vom Unruh-Spiralfeder-Typ
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EP2264553B1 (de) * 2009-06-19 2016-10-26 Nivarox-FAR S.A. Thermokompensierte Feder und ihr Herstellungsverfahren
JP6212473B2 (ja) * 2013-12-27 2017-10-11 株式会社神戸製鋼所 高強度ばね用圧延材及びこれを用いた高強度ばね用ワイヤ
EP2924514B1 (de) * 2014-03-24 2017-09-13 Nivarox-FAR S.A. Uhrfeder aus austenitischem Edelstahl
US20170067137A1 (en) * 2015-09-07 2017-03-09 Seiko Epson Corporation Titanium sintered body and ornament
EP3252542B1 (de) * 2016-06-01 2022-05-18 Rolex Sa Teil zur befestigung einer unruhspirale
FR3064281B1 (fr) * 2017-03-24 2022-11-11 Univ De Lorraine Alliage de titane beta metastable, ressort d'horlogerie a base d'un tel alliage et son procede de fabrication
EP3422116B1 (de) * 2017-06-26 2020-11-04 Nivarox-FAR S.A. Spiralfeder eines uhrwerks
EP3502288B1 (de) 2017-12-21 2020-10-14 Nivarox-FAR S.A. Herstellungsverfahren einer spiralfeder für uhrwerk
EP3502289B1 (de) * 2017-12-21 2022-11-09 Nivarox-FAR S.A. Herstellungsverfahren einer spiralfeder für uhrwerk
CH714492A2 (fr) * 2017-12-21 2019-06-28 Nivarox Sa Ressort spiral pour mouvement d'horlogerie et son procédé de fabrication.
EP3502785B1 (de) * 2017-12-21 2020-08-12 Nivarox-FAR S.A. Spiralfeder für uhrwerk, und ihr herstellungsverfahren
EP3502787B1 (de) * 2017-12-22 2020-11-18 The Swatch Group Research and Development Ltd Herstellungsverfahren einer unruh für uhren

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070133355A1 (en) * 2003-11-07 2007-06-14 Seik Epson Corporation Timepiece and spring thereof
CN107710081A (zh) * 2015-06-03 2018-02-16 Eta瑞士钟表制造股份有限公司 经由快慢针组件精细调节的谐振器

Also Published As

Publication number Publication date
JP7148577B2 (ja) 2022-10-05
CN112538587B (zh) 2022-08-16
CN112538587A (zh) 2021-03-23
JP2021051065A (ja) 2021-04-01
US20210088971A1 (en) 2021-03-25
CN114990402A (zh) 2022-09-02

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