Manufacturing method for watch parts

Abstract

A method for manufacturing a watch component made from an amorphous metal alloy is provided. [Solution] A method for manufacturing a watch part made of an amorphous metal alloy includes a step E1 of manufacturing a first preform made of an amorphous metal alloy, then a step E2 of heating and stretching the first preform to obtain a second preform, and then a step E3 of machining the second preform.

Description

[Technical Field]

[0001] The present invention relates to a method for manufacturing a timepiece component. The invention also relates to a timepiece component obtained by said method. The invention also relates to a speed regulating system comprising said timepiece component. The invention further relates to a timepiece movement comprising said speed regulating system or said timepiece component. The invention finally relates to a timepiece comprising said timepiece movement or said speed regulating system or said timepiece component. [Background technology]

[0002] Patent Document 1 proposes the production of bulk amorphous alloys based on zirconia and / or hafnium, which are nickel-free or nickel-free and beryllium-free. Patent Document 1 proposes, inter alia, increasing the critical diameter Dc of these amorphous alloys by adjusting their composition while maintaining high Tx-Tg values. Patent Document 1 states that the critical diameter Dc of the alloy must be larger than the maximum dimension of the part.

[0003] Patent document 2 relates to a method for producing a bar made of a non-magnetic amorphous alloy (metallic glass), in which the molten alloy is injected into a cooling mold to obtain an amorphous structure, and is then finished by one or more finishing steps. These are typically polishing or equivalent, and may optionally be preceded by machining, and may include surface hardening by ion bombardment (C, O, etc.), PVD, or carburization. The mentioned machining methods are, for example, turning, bar turning, or re-machining after bar turning with a cutting tool, or laser machining. It is also envisaged to vary the cooling rate in order to obtain an alloy with a crystalline or partially crystalline core and an amorphous surface. Particularly advantageously, the alloy Zr 57 Cu 20 Al 10 Ni8Ti5 is described.

[0004] Patent document 3 discloses the preparation of metallic glass wires of micro- and nanometer cross-sections by drawing. A feature of the method is the encapsulation or coating of one or more metallic glass preforms with a material having a viscosity similar to that of the preforms at the drawing temperature. One advantage of such a coating is the reduction of instabilities (breakage, reflow) during drawing. The coating may be made, for example, from a thermoplastic polymer or mineral glass. This allows the metallic glass wire to be continuously drawn down to nanometer diameters without breakage. After drawing, the coating can be mechanically or chemically removed. Furthermore, the coating may be retained with one or more metal fibers to form new hybrid materials. Such composite materials may have advantageous properties, especially in optical, electrical, or electrochemical fields. The following bulk metallic glasses were used in various exemplary embodiments: Au 49 Ag 5.5 Pd 2.3 Cu 26.9 Si 16.3 , Pt 57.5 Cu 4.7 Ni 5.3 P 22.5 . Alloy Zr 41.2 Ti 13.8 Cu 12.5 Ni 10 Be 22.5 , Pd 43 Cu 27 Ni 10 P 20 , Zr 35 Ti 30 Cu 8.25 Be 26.75 has also been proposed as being suitable for the production of micro- and nanometer wires, which utilizes the combination of a metallic glass and a coating material in a viscous state at the drawing temperature to stabilize the formation of sub-millimeter wires. [Prior art documents] [Patent documents]

[0005] [Patent Document 1] European Patent Application Publication No. 3128035 [Patent Document 2] Swiss Patent Application Publication No. 716669 [Patent Document 3] European Patent Application Publication No. 3856426 Summary of the Invention [Problem to be solved by the invention]

[0006] The object of the present invention is to provide a method for manufacturing a watch component, which allows for an improvement over the methods known from the prior art. In particular, the present invention proposes a method for manufacturing a watch component, which allows the watch component to be manufactured from metallic glass. [Means for solving the problem]

[0007] According to the invention, a method for manufacturing a watch component is defined in claim 1.

[0008] Embodiments of the manufacturing method are defined in claims 2 to 18.

[0009] According to the invention, the watch part is defined in claim 19.

[0010] The accompanying drawings show, by way of example, an embodiment of a timepiece according to the invention and an embodiment of a method for manufacturing timepiece components. [Brief explanation of the drawings]

[0011] [Figure 1] FIG. 1 is a schematic diagram of a timepiece according to the present invention. [Figure 2] FIG. 2 is a time-temperature-transformation diagram for an alloy capable of forming a metallic glass. [Figure 3] FIG. 3 is a time-temperature-transformation diagram similar to FIG. 2, with heat treatments indicated by lines. [Figure 4] FIG. 4 is a flowchart of one embodiment of the manufacturing method according to the present invention. DETAILED DESCRIPTION OF THE INVENTION

[0012] One embodiment of the watch 400 is described in detail below with reference to FIG.

[0013] The timepiece 400 is for example a small timepiece, in particular a wristwatch, and includes a timepiece movement 300 that is intended to be mounted in a timepiece casing or case to protect it from the external environment.

[0014] The watch movement 300 is a mechanical movement, in particular an automatic movement, or a hybrid movement.

[0015] The timepiece movement 300 comprises the regulating system 200, among other things: - oscillators, in particular spring-balance-wheel oscillators, and an escapement, in particular an escapement comprising at least one escape wheel and pallet assembly; The speed control system includes:

[0016] The regulating system 200 comprises at least one timepiece part 100 obtained by implementing the manufacturing method that is the subject of the present invention. The timepiece part 100 may, for example, comprise a shaft, among others: - Tenma, or - Escape wheel shaft, or - Anchor or true is.

[0017] The speed governor system 200 may thus include all or some of the following components manufactured according to the method that is the subject of the present invention: - Tenshin, and / or - escape wheel shaft, and / or - Uncle axle or true.

[0018] The timepiece part 100 may also be a pinion of a moving part, in particular an escape wheel pinion.

[0019] The clock movement 300 may alternatively also be of the electronic type and may include a clock component 100 manufactured according to the method that is the subject of the present invention.

[0020] Several studies have shown that magnetic fields can disrupt the operation of mechanical timepieces, primarily due to their effect on their regulating systems. The parts of the regulating system that are most sensitive to magnetic fields are the balance spring, the escape wheel, and the pallet assembly. The sensitivity of the shafts of these elements to magnetic forces plays a key role. This is why it is important to make these shafts insensitive to magnetic fields.

[0021] The present invention therefore relates to a method for manufacturing or producing a non-magnetic timepiece component, in particular a shaft intended for the moving part of a timepiece's speed regulating system, said method being notable in that it makes it possible to take advantage of the thermal stability of bulk amorphous metals, also called bulk metallic glasses, which allow the drawing of a billet to obtain a bar, which is then machined by conventional methods, in particular by bar turning, to obtain a timepiece shaft. Such a manufacturing or production method comprises: 1) Cross sections with dimensions larger than typical watch dimensions, especially centimeter dimensions (e.g., approximately 0.3 cm each) 2 20cm from 2

[0033] producing or producing a first preform made of bulk amorphous metal having a cross section of between 0.6 cm and 5 cm in diameter and a surface area of ​​between 0.6 cm and 5 cm; 2) especially millimeter dimensions (e.g., approximately 0.8 mm each) 2 from 20mm 2 heat-stretching the first preform to obtain a second preform having a cross-section whose dimensions approximate those of the watch part, the second preform having a cross-section of between 1 and 5 mm (a diameter of between 1 and 5 mm, a surface area of ​​between 1 and 5 mm); 3) machining a shaft from the second preform by bar turning; 4) Friction finish, The method may include the following four steps:

[0022] The material of the shaft of the moving part of the regulating system of a watch should ideally have the following properties, among others: - Non-magnetic, - have good mechanical properties, in particular good impact resistance and compressive strength, - Excellent tribological behavior, - Easily formable to low tolerances, typically by bar turning; - Has good corrosion resistance.

[0023] The traditional material for the moving shaft of a regulating system is quenchable, free-cutting steel (e.g., 20AP or Finemac). However, these materials are magnetic, which poses significant problems for the operation of the watch. In addition, they are sensitive to humidity, necessitating the use of special packaging, e.g., in a protective atmosphere. Furthermore, these materials are machined in a ferritic state, which is too soft for the requirements of the moving shaft. For this reason, they must be hardened throughout using a quenching and tempering process before the rolling step.

[0024] Amorphous metals are generally harder overall than crystalline alloys. These materials exhibit unique mechanical properties, such as high elastic limits, high hardness, and elastic deformations approaching 2%.

[0025] Amorphous metal alloys have good properties in terms of insensitivity to magnetic fields depending on their composition. For this reason, these alloys have excellent potential to replace quenchable free-cutting steels, especially in applications related to the moving shafts of clock-governing systems. However, until now, it has not been possible to use amorphous metal alloys using standard machining techniques.

[0026] Figure 2 shows the time (horizontal axis) vs. temperature (vertical axis) transformation diagram, which shows that alloys capable of forming metallic glasses are: - liquid (above temperature threshold TL), - Amorphous (below the temperature threshold Tg) - crystalline (upper right of the area delimited by the curved shape), - supercooled liquid (elsewhere in the diagram), The following shows the four phases:

[0027] The dashed-dotted lines indicate the temperature-time profile during the cooling step. Line A indicates the cooling to obtain the amorphous state. Line B indicates the critical cooling (the minimum cooling rate to achieve a completely amorphous structure).

[0028] In FIG. 3, which shows the same view, the dashed dotted lines indicate the temperature-time profile during the steps of heat drawing (line C) and partial crystallization heat treatment (line D).

[0029] The application of metallic glasses is limited by the difficulty of manufacturing such alloys. The amorphous structure that characterizes these alloys is obtained by rapid cooling from the liquid state, for example, according to line A in Figure 2. The material is thus frozen without giving the atoms time to align. This metastable structure, in contrast to crystalline materials, does not have long-term order. For some alloys, the critical cooling rate to prevent the crystallization front (see line B tangent to the curved shape) is several thousand K / s.

[0030] If the cooling is not rapid enough, the material will partially or totally crystallize, which is generally detrimental to its properties, especially its mechanical properties (e.g., brittleness). However, in some cases, controlled partial crystallization is desired to adapt the mechanical properties to the application. For this purpose, the amorphous material may be heated in a controlled manner from ambient temperature to a temperature above the glass transition temperature Tg. In this way, the material is brought into the supercooled region and held for a predetermined time, depending on the temperature, so that crystals can form and grow (see line D in Figure 3).

[0031] As mentioned above, the high cooling rates required to obtain an amorphous structure, especially on the millimeter scale, limit the practical application of such alloys. Within the family of metallic glasses, there is a subclass called bulk metallic glasses (BMGs) that have high thermal stability (glass-forming ability, GFA), which indicates the resistance of the material to crystallization. This concept can be characterized by the measurement of the critical diameter Dc, defined as the maximum diameter of a cylinder that can be cast to obtain a completely amorphous material.

[0032] The critical cooling rate of bulk metallic glasses is therefore lower than that of "standard" metallic glasses, which makes it possible to fabricate millimeter- or even centimeter-sized semi-finished (near-net-shape) parts, for example by injection from the liquid state or by thermoforming in the supercooled state.

[0033] Alternatively, the use of force-free machining methods, typically with femtosecond lasers, can be proposed. However, given the low material removal rates, these methods must be applied to preforms with dimensions that are fairly close to the desired dimensions of the final part, such as those that can be obtained by the methods described above. Electrolytic corrosion is also a suitable method for metallic glasses, especially for cutting two-dimensional parts from plates.

[0034] Until now, there has been no method for producing metallic glass rods several meters long and with millimeter cross sections that can be used to fabricate parts by traditional machining processes such as bar turning. Additionally, those skilled in the art have dismissed metallic glasses due to their poor suitability for machining, fragility, high hardness, and temperature sensitivity.

[0035] Applicant's research has shown that it is still possible to perform hot drawing of bulk metallic glasses with high thermal stability in the supercooled region, and that the high thermal stability allows sufficient time for the hot drawing step to be performed without crystallizing the material.

[0036] This allows, by choosing the appropriate alloy, to produce machinable bars by conventional means (bar turning).

[0037] One embodiment of the method is described in detail below with reference to Figure 4. The method involves the deposition of amorphous palladium-based alloys, particularly Pd 43 Cu 27 Ni 10 P 20 (atomic %). Its main properties are: - Good wear resistance and low coefficient of friction under typical watch conditions, e.g. ruby ​​pivots - Hardness: about 500HV, - Elastic limit: approx. 2000 MPa, - non-magnetic, - Excellent thermal stability, is.

[0038] In the preparation step E1, the alloy was melted at approximately 1000°C and then cast in a water-cooled copper mold. The material was cooled at a rate faster than the critical cooling rate of the alloy. A first preform in the form of an amorphous billet with a diameter of 10 mm was then produced. The length of these preforms in the tests ranged from 10 to 20 cm. XRD (X-ray diffraction) and DSC (differential scanning calorimetry) analyses made it possible to confirm the amorphous state of these samples. The glass transition temperature Tg and the transition temperature Tx measured by DSC under argon at a rate of 20°C / min were Tg = 316 ± 5°C and Tx = 420 ± 5°C, respectively.

[0039] In the second step E2, which corresponds to the thermoforming step, the first preform was subjected to heating and stretching. The preliminary stretching tests were carried out on a machine specially constructed for stretching nanometer polymers and / or nanometer glass fibers. The machine consists of a vertical frame, on the top of which a heating system is located and on the bottom of which a stretching system (e.g., pulleys or capstans) is located. A tension sensor is installed between the heating and stretching systems.

[0040] Feasibility tests were carried out without coating and without gas protection. The first preform used had a diameter of 10 mm and a length of 20 cm.

[0041] The first preform, held on its top by the jaws, is placed vertically in a heating system. The heating system may consist of different heating elements to have zones of different temperatures. The central zone is the hottest zone where the drawing process is carried out. A typical temperature in this zone is 380°C. The temperature of the zones may vary during the drawing process depending on the dimensions of the preform and the metal. The temperature of the central zone is 10 7 ~10 4 It is controlled in the range Tx~Tg to reach an amorphous alloy viscosity in the range of Pa·s.

[0042] To initiate drawing, a force must be applied to the first preform. One solution is to drill a hole in the bottom of the preform to allow the passage of a wire supporting a weight.

[0043] The feed rate and drawing rate of the preform in the heating system are adjustable parameters depending, inter alia, on the diameter of the preform and the desired diameter of the drawing wire, for example 2 mm / min and 60 mm / min, respectively.

[0044] The first preform is hot drawn in air without a die. Several second preforms (in the form of wires) are obtained with diameters varying between 1.7 and 1.9 mm over a total length of about 1.5 m.

[0045] In a third step E60, centerless grinding is carried out. Thus, cylindrical grinding techniques are carried out to obtain wire with the appropriate dimensional tolerances required to enable machining of high-precision parts by bar turning. For free-cutting wire, a tolerance of h6 (+0; -6 μm for a 2 mm φ wire) over a length of at least 1 m is typical.

[0046] In a fourth step E3, the shaft, and in particular the balance shaft, is machined, in particular dry machined, on a lathe using diamond or coated tools.

[0047] In a fifth step E5, finishing is carried out, in particular a rub-finishing of the part obtained at the end of the fourth step E4.

[0048] One exemplary embodiment applied to a Pd-based metallic glass has been described above, however the fabrication method is applicable to any other bulk metallic glass, in particular any alloy listed in the table below.

[0049] [Table 1]

[0050] The list is not exhaustive. Preferably, the metals used have the following properties: - Supercooled region ΔTx ≥ 40k (where ΔTx = Tx - Tg), and - Critical diameter greater than 6mm.

[0051] One exemplary embodiment has been described in which heat stretching is used as the thermoforming step, however, thermoforming steps of other nature may also be used, especially extrusion.

[0052] A more general embodiment of the method according to the invention will now be described, again with reference to Figure 4. The embodiment applies to bulk amorphous metal alloys having a supercooling region ΔTx = Tx - Tg above 40°C, preferably above 60°C, more preferably above 100°C. The method is a method for producing a timepiece component, in particular a balance shaft, of a moving part of a regulating system.

[0053] In a preparation step E0, a pre-alloy of amorphous or partially amorphous alloy is produced, for example by vacuum induction melting (VIM) or by arc melting.

[0054] In a first step E1, a first preform is formed either by static casting in a mold, or by quasi-continuous molding or injection. The first preform is then composed of the alloy in an amorphous state. The first preform is preferably in the form of a rod, more preferably of circular cross section, with a diameter and length greater than 6 mm and 10 cm, more preferably greater than 10 mm and 20 cm, respectively.

[0055] In one embodiment, the first step E1 comprises a first sub-step E11 dedicated to structuring the first preform. In one variant, the surface of the first preform is textured to obtain a predetermined configuration, which is stretched during the second step E2 of thermoforming (in particular hot-drawing) to obtain the desired surface structure. In another variant, the structuring may be the shape of a cross-section with a specific profile, such as a toothed profile, which is maintained by homothetic deformation during the second step E2 of thermoforming by hot-drawing. In the first sub-step E11, the structuring of the first preform may be obtained, for example, by machining or stamping, to obtain, for example, toothed gears, pinion teeth, profiled elements.

[0056] In one embodiment, the second substep E12 may comprise a partial crystallization of the material of the first preform by heat treatment in order to increase the hardness of the material, for example with a crystalline phase content of less than 60%, preferably less than 40%, more preferably less than 30%, even more preferably less than 5%, the percentages being expressed by volume of the material. In preliminary tests, pellets with a diameter of 10 mm and a thickness of 3 mm underwent a hardness increase of approximately 10% after being subjected to a heat treatment at 370°C for 40 minutes under vacuum, followed by rapid cooling at over 100°C / min. The pellets after heat treatment had a crystalline phase volume fraction of approximately 40%. In a second step E2, the first preform is thermoformed, in particular by dieless hot drawing in a controlled atmosphere, or under vacuum, or in air, to obtain a second preform. Preferably, in said thermoforming, the first preform is heated between the glass transition temperature Tg and the crystallization temperature Tx. Preferably, the second preform has at least one dimension which exceeds the critical diameter Dc of the amorphous alloy (composing the second preform) by a factor of more than 5, preferably by a factor of more than 10, or by a factor of more than 100, or by a factor of more than 1000. Preferably, the second preform is of circular cross section, in particular - diameter greater than 1 mm, preferably greater than 2 mm, and - of a length of more than 0.5 m, preferably more than 1 m or more than 2 m, In another embodiment, the second step E2 comprises a heated drawing in a controlled atmosphere, even in a vacuum, to protect the bulk metallic glass from oxidation.

[0057] In one embodiment, in the second step E2, a fourth heat treatment substep E21 is carried out in which the second preform is partially crystallized before the third machining step E3 in order to increase the hardness of the second preform.

[0058] In a third step E3, the second preform is machined by a forceful method, i.e. the second preform is machined by chip removal or by abrasion, for example by grinding. The machining step E3 may include a sub-step E31 of bar turning.

[0059] The third step E3 may also optionally be followed by a sub-step E31: - To obtain dimensional tolerances, and / or - In the case of shafts, to improve the surface conditions of the pivots, It may also include a sub-step E33 of rolling the preform.

[0060] The third step E3 may also comprise, optionally after sub-step E31 and / or before sub-step E33, an additional sub-step E32 of cutting teeth, for example cutting teeth of an escape wheel pinion.

[0061] The third step E3 may also optionally be preceded by a step E4 of consolidation of the preform by partial crystallization heat treatment, optionally after substep E31 and / or after substep E32 and / or after substep E33.

[0062] In a fifth step E5, a finishing step, in particular a rub-finishing step, of the preform is carried out in order to remove burrs and to guarantee an optimum surface condition of the finished watch part.

[0063] In one embodiment, in an additional sixth step E6, the part resulting from the third step E3 or the watch part resulting from the fourth step E4 or the fifth step E5 is surface-hardened, for example by thermochemical treatment or ion implantation. In one embodiment, the surface-hardening may be preceded by a rubbing step.

[0064] Regardless of the embodiment or modification, the manufacturing method includes: a) In a first step E1, the first preform is coated with a material having a viscosity comparable to that of the metal alloy at the drawing temperature, for example a polymer coating (e.g., Pt 57.5 Cu 14.7 Ni 5.3 P 22.5 a third substep E13 of coating the first preform with a mineral glass coating (e.g., PEI (polyetherimide) on a platinum-based metallic glass preform) or with a mineral glass coating (e.g., phosphate glass on a palladium-based metallic glass preform), b) in a second step E2, stretching the first binary (coated) preform, and c) A fifth substep E30 of removing the coating in the third step E3, for example by dissolution, by chemical attack or by machining, to release the metal parts. For example, the PEI coating can be dissolved in a solution of N-methyl-2-pyrrolidone. may include:

[0065] Regardless of the embodiment or variant, the manufacturing method may comprise, between the second step E2 and the third step E3, an additional step E60 of grinding, for example centerless grinding, the second preform, in order to produce a modified preform. In particular, the modified preform has a circular cross section, typically with a diameter h6 (for a diameter of 2 mm, +0 μm; −6 μm), within the tolerances required for automatic precision bar turning.

[0066] Regardless of the embodiment or variant, the manufacturing method may include, after step E2 or after step E60, an additional step E70 of cold drawing through a die to obtain a narrower tolerance range of +0 μm; -3 μm in diameter to form a further modified preform, during which the reduction in cross section is less than 20%, preferably less than 10%, more preferably less than 5%. In one embodiment, in this step E70, the second or modified preform is drawn through a die having a contoured shape, for example a toothed shape.

[0067] The method according to the invention relates to the manufacture of timepiece parts, in particular timepiece shafts. Before the end of the method, the partially manufactured timepiece part is referred to as a "preform". In particular, at the end of the first step E1, the partially manufactured timepiece part is referred to as a "first preform", and at the end of the second step E2, the partially manufactured timepiece part is referred to as a "second preform".

[0068] In the figure, steps and sub-steps indicated by dotted boxes are optional steps.

[0069] As can be inferred from the above explanation, "heat-stretching" is understood herein to mean a process different from extrusion, in particular in that heat-stretching does not use a die. The absence of a die makes it possible to obtain a better surface condition by preventing contact interaction with the die. The absence of interaction also makes it possible to prevent the crystallization temperature Tx from being exceeded. Finally, the absence of interaction makes it possible to prevent contamination. [Explanation of symbols]

[0070] 100 watch parts 200 Speed ​​Control System 300 clock movements 400 Clocks

Claims

1. A method for manufacturing a watch component (100) made of an amorphous metal alloy, said method comprising the steps of: A step (E1) of producing a first preform made of an amorphous metal alloy, and then A step (E2) of heating and stretching said first preform to obtain a second preform, and then a step (E3) of machining said second preform; Including, method.

2. the amorphous metal alloy has a supercooling region ΔTx=Tx-Tg greater than 40°C, greater than 60°C, or greater than 100°C, where Tx is the crystallization temperature and Tg is the glass transition temperature; The method of claim 1.

3. The amorphous metal alloy is a Pd-based alloy, or a Pt-based alloy, or a Zr-based alloy, for example, in atomic percent: Pd ４３ Ni １０ Cổ ２７ P ２０ 、 Pt ５７．５ Cu １４．７ Ni ５．３ P ２２．５ 、 Pd ７５ Si １５ Ag ３ Cu ７ 、and Zr ４１．２ Ti １３．８ Cu １２．５ Ni １０ Be ２２．５ 、 The composition is 3. The method according to claim 1 or 2.

4. The first step (E1) comprises a substep (E11) of structuring the first preform, in particular by machining or stamping, 4. The method according to any one of claims 1 to 3.

5. said first step (E1) comprises a substep (E12) of hardening said material of said first preform by a crystallization heat treatment, in particular by a partial crystallization heat treatment; 5. The method according to any one of claims 1 to 4.

6. the second step (E2) comprises a dieless hot drawing, in particular at a temperature between the glass transition temperature and the crystallization temperature, to obtain a second preform in which at least one dimension exceeds the critical diameter of the amorphous cortical alloy by a factor of more than 5, or more than 10, or more than 100, or more than 1000; 6. The method according to any one of claims 1 to 5.

7. The second preform is preferably of circular cross section, diameter greater than 1 mm or greater than 2 mm, and / or a length greater than 0.5 m or greater than 1 m or greater than 2 m; a rod, bar or wire having 7. The method according to any one of claims 1 to 6.

8. the step (E1) of producing the first preform made of amorphous metal alloy comprises a coating (E13) of the amorphous metal alloy with a thermoplastic material, for example a polymer or a mineral glass; 8. The method according to any one of claims 1 to 7.

9. said machining step (E3) comprises a substep (E30) of removing said coating, for example by dissolution, by chemical attack or by machining; The method of claim 8.

10. The heating and stretching step (E2) comprises a substep (E21) of hardening by partial crystallization heat treatment; 10. The method according to any one of claims 1 to 9.

11. The method further comprises the steps of: between the heating and stretching step (E2) and the machining step (E2), a grinding substep (E60), and / or a substep (E70) of drawing through a mold, further comprising an additional molding step, 11. The method according to any one of claims 1 to 10.

12. The machining step (E3) comprises machining, in particular turning (E31), by applying a force; 12. The method according to any one of claims 1 to 11.

13. The machining step (E3) comprises rolling (E32), 13. The method according to any one of claims 1 to 12.

14. said machining step (E3) comprises cutting the toothing (E33), for example cutting the pinion; 14. The method of any one of claims 1 to 13.

15. The method comprises, after the machining step (E3), a step (E4) of hardening by partial crystallization heat treatment, 13. The method according to any one of claims 1 to 12.

16. The method comprises, after the curing step (E4), a finishing step (E5), in particular by rubbing, 16. The method of claim 15.

17. The method may comprise, after the machining step (E3), a finishing step (E5), for example a friction finishing step, 17. The method of any one of claims 1 to 16.

18. The method comprises a preparation step (E0) of producing a pre-alloy of said amorphous or partially amorphous alloy, for example by vacuum induction melting (VIM) or by arc melting, 18. The method of any one of claims 1 to 17.

19. A timepiece part (100), in particular a shaft (100) of a speed regulating system (200) of a timepiece (400), such as a balance or pallet or moving part pinion, obtained by carrying out the method according to any one of claims 1 to 18.

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