Method of manufacture of a watch_making component

Abstract

Method for making a watch component (100) in amorphous metal alloy, the manufacturing process comprising: - a step (E1) of making a first preform in amorphous metal alloy, then - a step (E2) of hot drawing of the first preform to obtain a second preform, then - a step (E3) of machining of the second preform.

Description

[0001] The invention relates to a method for manufacturing a watch component. The invention also relates to a watch component obtained by such a method. The invention also relates to a regulating system comprising such a watch component. The invention further relates to a watch movement comprising such a regulating system or such a watch component. Finally, the invention relates to a timepiece comprising such a watch movement, such a regulating system, or such a watch component.

[0002] Patent application EP3128035A1 proposes the fabrication of bulk amorphous zirconium and / or hafnium alloys, free of nickel, or both nickel and beryllium. It specifically proposes increasing the critical diameter De of these amorphous alloys by adjusting their composition, while maintaining a high Tx-Tg value. It states that the critical diameter De of the alloy must be greater than the largest dimension of a component.

[0003] Patent application CH716669A1 relates to a method for manufacturing a balance staff from a non-magnetic amorphous alloy (metallic glass), in which the molten alloy is injected into a cooled mold to obtain an amorphous structure, then finished with one or more finishing steps. These typically include polishing or equivalent, with or without prior machining, and may include surface hardening by ion bombardment (C, O, ...), PVD, or carburizing. Machining methods mentioned include turning, bar turning or re-bar turning using cutting tools, or laser machining, for example. Varying the cooling rate to obtain a crystalline or partially crystalline alloy at its core and an amorphous surface is also considered. The alloy Zr 57 Cu 20 Al 10 Ni 8 Ti 5 is mentioned as being of particular interest.

[0004] Patent application EP3856426A1 describes the preparation of micro- and nanometer-sized metallic glass fibers by drawing. The distinctive feature of the process is the coating, or sheathing, of one or more metallic glass preforms with a material having a viscosity similar to the preforms at the drawing temperature. One advantage of this sheath is that it reduces instabilities (breakage, sloughing) during drawing. The sheath can be made, for example, of a thermoplastic polymer or a mineral glass. This allows metallic glass fibers to be drawn continuously to a nanometer diameter without breaking. After drawing, the sheath can be removed mechanically or chemically. Furthermore, the sheath can be retained to form a new hybrid material with one or more metallic fibers. This composite can have interesting properties, particularly in the optical, electrical, or electrochemical fields.The following solid metallic glasses have been used in various 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. The alloys Zr 41.2 Ti 13.8 Cu 12.5 Ni 10 Be 22.5, Pd 43 Cu 27 Ni 10 P 20, and Zr 35 Ti 30 Cu 8.25 Be 26.75 have also been proposed as suitable for the production of micro- and nanometer-sized wires. This patent application takes advantage of the combination of the viscous state of the metallic glass and the coating material at the drawing temperature to stabilize the formation of submillimeter-sized wires.

[0005] The object of the invention is to provide a method for manufacturing a watch component that improves upon known prior art methods. In particular, the invention proposes a method for manufacturing a watch component that allows the watch component to be made of a metallic glass.

[0006] According to the invention, a method for making a watch component is defined by claim 1.

[0007] Methods of executing the manufacturing process are defined by claims 2 to 18.

[0008] According to the invention, a watch component is defined by claim 19.

[0009] The attached drawings represent, by way of example, an embodiment of a timepiece according to the invention and an execution method of a process for making a timepiece component. There figure 1 is a schematic view of a timepiece according to the invention. figure 2 is a time, temperature, and transformation diagram of an alloy capable of forming a metallic glass. figure 3 is a time, temperature and transformation diagram, like that of the figure 2 , and on which heat treatments have been represented by lines. The figure 4 is a flowchart of an execution method of a manufacturing process according to the invention.

[0010] An embodiment of a 400 timepiece is described below in detail with reference to the figure 1 .

[0011] A timepiece 400 is, for example, a watch, specifically a wristwatch. A timepiece 400 includes a watch movement 300 intended to be mounted in a case or box to protect it from the external environment.

[0012] The 300 watch movement is a mechanical movement, specifically an automatic movement, or a hybrid movement.

[0013] The 300 watch movement includes a 200 regulating system, specifically a regulating system comprising: an oscillator, in particular a balance-spring oscillator, and an escapement, in particular an escapement comprising at least one escape wheel and one anchor.

[0014] The regulating system 200 comprises at least one watch component 100 obtained by implementing the manufacturing process of the invention. The watch component 100 is, for example, a shaft, in particular: a balance wheel axle, or an escape wheel axle, or an anchor axle or rod.

[0015] The regulating system 200 may thus comprise all or part of the following components, manufactured according to the process that is the subject of the invention: a balance staff, and / or an escape wheel staff, and / or an anchor staff or stem.

[0016] The watch component 100 can also be a pinion of a moving part, in particular an escape wheel pinion.

[0017] The watch movement 300 can alternatively be of the electronic type and include a watch component 100 made according to the process which is the subject of the invention.

[0018] Several studies have shown that magnetic fields can disrupt the operation of a mechanical watch, primarily through their impact on its regulating system. The components most sensitive to magnetic fields are the balance wheel and hairspring, the escape wheel, and the pallet fork. The sensitivity of the axes of these components to magnetism plays a crucial role. Therefore, it is essential to make these axes insensitive to magnetism.

[0019] To this end, the invention relates in particular to a method for manufacturing or producing a non-magnetic watch component, specifically a shaft for the moving parts of a timepiece's regulating system. This method is remarkable in that it takes advantage of the thermal stability of solid amorphous metals, also known as solid metallic glasses, to allow the drawing of bars, which are then machined by a traditional process, particularly by turning, to obtain watch shafts. Such a manufacturing or production method may comprise four steps: 1) manufacturing or producing a first preform in solid amorphous metal with a cross-section larger than typical watchmaking dimensions, in particular with a cross-section of centimetric dimensions (for example, a diameter between 0.6 cm and 5 cm, respectively of approximately between 0.3 cm² and 20 cm² of surface area), 2) hot drawing of this first preform in order to obtain a second preform with a cross-section of dimensions approaching the dimensions of a watch component, in particular with a cross-section of millimetric dimensions (for example, a diameter between 1 and 5 mm, respectively of approximately between 0.8 mm² and 20 mm² of surface area), 3) machining by turning of a shaft from the second preform, 4) tribofinishing.

[0020] The material of the axes of the moving parts of the regulating system of the timepiece should, among other things, ideally have the following properties: to be non-magnetic, to possess good mechanical properties, including good shock and compression resistance, to have excellent tribological behavior, to be easily formed with small tolerances, typically by turning, to have good corrosion resistance.

[0021] The traditional material for the pivots of the regulating system is hardenable free-cutting steel (e.g., 20AP or Finemac). However, these materials are magnetic, which is critical for the operation of a timepiece. Furthermore, they are sensitive to humidity, requiring special packaging, such as a modified atmosphere. In addition, these materials are machined in a ferritic state, which is too soft for the requirements of pivot pivots. Therefore, it is necessary to harden them throughout by quenching and tempering them before rolling.

[0022] Amorphous metals are generally harder throughout their mass compared to crystalline alloys. These materials exhibit unique mechanical properties such as high yield strength, high hardness, and elastic deformation close to 2%.

[0023] Amorphous metal alloys can exhibit good resistance to magnetic fields, depending on their composition. These alloys therefore have strong potential to replace hardenable free-cutting steels, particularly for applications such as the shafts of moving parts in watchmaking regulating systems. However, until now, amorphous metal alloys could not be used with standard machining techniques.

[0024] On the figure 2 We illustrated, using a diagram of time (on the x-axis), temperature (on the y-axis) and transformation, the four phases in which an alloy capable of forming a metallic glass can be found: liquid (above the temperature threshold TL), amorphous (below the temperature threshold Tg), crystalline (top right in the area delimited by the curved shapes), and supercooled liquid (elsewhere on the diagram).

[0025] The dashed lines illustrate temperature-time profiles during cooling stages. Line A illustrates cooling that results in an amorphous state. Line B illustrates critical cooling (the lowest cooling rate that leads to a fully amorphous structure).

[0026] On the figure 3 representing the same diagram, dashed line plots illustrate temperature-time profiles during hot drawing (plot C) and partial crystallization heat treatment (plot D).

[0027] The applications of metallic glasses are limited due to the difficulties in processing such alloys. The amorphous structure that characterizes these alloys is obtained by rapid cooling from the liquid state, for example along line A on the figure 2 Thus, the material solidifies without giving the atoms time to organize themselves. This metastable structure therefore lacks long-range order, unlike crystalline materials. For some alloys, the critical cooling rate, in order to avoid the crystallization nose (see line B tangent to curved shapes), is several thousand K / s.

[0028] If cooling is not rapid enough, the material partially or completely crystallizes, which is generally detrimental to its properties, including its mechanical properties (brittleness). However, in some cases, controlled partial crystallization is desirable to tailor the mechanical properties to the application. To achieve this, the amorphous material can be heated in a controlled manner from room temperature to a temperature above the glass transition temperature (Tg). The material is thus brought into the supercooled region and held there for a specific time, depending on the temperature, so that crystals can form and grow (see plot D on the diagram). figure 3 ).

[0029] As discussed above, the high cooling rates required to obtain an amorphous structure limit the implementation of such alloys, particularly at the millimeter scale. Within the family of metallic glasses, there is a subclass called bulk metallic glasses (BMG), which exhibit high thermal stability (Glass Forming Ability, GFA), representing the material's resistance to crystallization. This can be characterized by measuring a critical diameter De, defined as the maximum diameter of a cylinder that can be cast to obtain a completely amorphous material.

[0030] The critical cooling rate for bulk metallic glasses is therefore lower than for "standard" metallic glasses. As a result, semi-finished (near-net shape) components of millimeter or even centimeter size can be produced, for example by injection molding from the liquid state or by thermoforming in the supercooled state.

[0031] Alternatively, the use of forceless machining processes, typically femtosecond lasers, can be considered. However, given the low material removal rate, these processes need to be applied to preforms with dimensions fairly close to the desired final part dimensions, such as those obtainable by the processes mentioned above. Electrical discharge machining (EDM) is also a suitable method for metallic glass, particularly for cutting 2D components from a wafer.

[0032] Therefore, no process existed for manufacturing metal-glass bars several meters long with a millimeter cross-section, which could then be used to manufacture components by traditional machining, such as bar turning. Furthermore, skilled craftsmen rejected metal-glass due to its poor machinability, resulting from its fragility, high hardness, and thermal sensitivity.

[0033] The applicant's research has shown that it is nevertheless possible to carry out hot drawing in the supercooled field of massive metallic glasses possessing high thermal stability, the high thermal stability allowing sufficient time to implement this hot drawing step without the material crystallizing.

[0034] This allows, by selecting a suitable alloy, the production of bars that can then be machined by a conventional means (turning).

[0035] One method of implementing the process is described in more detail below with reference to the figure 4 It is applied to an amorphous palladium-based alloy, specifically Pd₄³Cu₂₇Ni₁₀P₂O (at%). Its main characteristics are: Good wear resistance and low coefficient of friction under typical watchmaking conditions, for example a pivot in a ruby, Hardness: about 500 HV, Yield strength: about 2000 MPa, Non-magnetic, High thermal stability.

[0036] In a preliminary step E1, an alloy is melted at approximately 1000°C and then poured into a water-cooled copper ingot mold. The material is cooled at a rate higher than the critical cooling rate for this alloy. This produces initial preforms in the form of amorphous bars with a diameter of 10 mm. The length of these preforms in the tests ranged from 10 to 20 cm. XRD (X-ray Diffraction) and DSC (differential scanning calorimetry) analyses confirm the amorphous state of these samples. The glass transition temperatures (Tg) and transition temperatures (Tx) measured by DSC at a rate of 20°C / min under argon are Tg = 316 ± 5°C and Tx = 420 ± 5°C, respectively.

[0037] In a second step, E2, corresponding to a thermoforming stage, the first preforms undergo hot drawing. Exploratory drawing tests were carried out on a machine specifically designed for drawing nanometric polymer and / or metallic glass fibers. The machine consists of a vertical frame with a heating system positioned at the top and a drawing system at the bottom (for example, a pulley or a capstan). A tension sensor is placed between the heating and drawing systems.

[0038] Feasibility tests were carried out without sheathing and without gas shielding. The first preforms used had a diameter of 10 mm and a length of 20 cm.

[0039] The first preform, held at its upper end by a clamp, is placed vertically in the heating system. This system may consist of several heating elements to create zones with different temperatures. The middle zone is the hottest area where the drawing process takes place. A typical temperature for this zone is 380 °C. The temperature of the zones depends on the dimensions of the preform and the alloy, and it can change during the drawing process. The temperature in the middle zone is controlled within the range Tx - Tg to achieve the viscosity of the amorphous alloy in the range of 10⁷ to < 10⁴ Pa·s.

[0040] To initiate the drawing process, a force must be applied to the first preform. One solution is to make a hole in the lower part of the preform, allowing a wire supporting a weight to be passed through.

[0041] The feed rate of the preform in the heating system and the drawing rate are adjustable parameters depending on, among other things, the diameter of the preform and the desired diameter of the drawn wire, and are for example 2 mm / min and 60 mm / min respectively.

[0042] The first preform is hot-drawn without a die and under air. Several second preforms (in the form of wires) are obtained with a diameter varying between 1.7 and 1.9 mm along their entire length, approximately 1.5 m.

[0043] In a third step, E60, centerless grinding is performed. This involves implementing a cylindrical grinding technique to obtain wires with the appropriate dimensional tolerances necessary for subsequently machining high-precision components by screw machining. A tolerance h6 (+0; -6 µm for a 2 mm diameter wire) over a length of at least 1 m is typical for screw-machining wires.

[0044] In a fourth step E3, axes, including balance shafts, are machined, notably dry, on a screw machine, with diamond or coated tools.

[0045] In a fifth step E5, a finishing process is carried out. Specifically, the parts obtained at the end of the fourth step E4 undergo a tribofinishing.

[0046] An example of this embodiment has been described above, applied to a Pd-based metallic glass. However, the fabrication process can be applied to any other bulk metallic glass, in particular to any alloy listed in the table below. Composition [%at] D c [mm] T g [K] T L [K] D T x [K] Pd 43 Ni 10 Cu 27 P 20 30 305 554 131 Pt 57.5 Cu 14.7 Ni 5.3 P 22.5 20 236 540 98 Pd 75 Si 15 Ag 3 Cu 7 10 348 756 74 Zr 41.2 Ti 13.8 Cu 12.5 Ni 10 Be 22.5 14 349 714 77

[0047] This list is not exhaustive. Preferably, the alloy used has the following characteristics: a supercooling domain ΔTx≥40 K (with ΔTx= Tx-Tg), and a critical diameter greater than 6 mm.

[0048] An example of this process was described above using hot drawing as the thermoforming step. However, a different type of thermoforming step can be implemented, such as extrusion.

[0049] A more general embodiment of the method according to the invention is further described below, also with reference to the figure 4 It applies to a massive amorphous metallic alloy having a supercooling range ΔTx = Tx-Tg greater than 40°C, preferably greater than 60°C, and even more preferably greater than 100°C. The process is a method for manufacturing a watch component, in particular a pivot of a regulating system, especially a balance staff.

[0050] In a preliminary step E0, a pre-alloy of the amorphous or partially amorphous alloy is produced, for example by vacuum induction melting (Vacuum Induction Melting VIM) or by arc melting (arc-melter).

[0051] In the first step E1, a first preform is formed either by static casting in an ingot mold, by semi-continuous casting, or by injection molding. The first preform consists of an alloy in an amorphous state. The first preform is preferably in the form of a bar, more preferably in the form of a round bar with a diameter and length greater than 6 mm and 10 cm respectively, and even more preferably greater than 10 mm and 20 cm.

[0052] In one execution mode, the first step E1 includes a first substep E11 dedicated to structuring the first preform. In one variant, the surface of the first preform is textured to obtain a predefined structure, which is then stretched in a second thermoforming step E2 (in particular, hot stretching) to obtain the desired surface structure. In another variant, the structuring can take the form of a section with a specific profile, such as a toothed profile, which is then maintained by homothetic deformation in the second hot stretching thermoforming step E2. In the first substep E11, the structuring of the first preform can be achieved, for example, by machining or stamping, to produce gears, pinion teeth, or profiles.

[0053] In one embodiment, a second substep E12 may include partial crystallization of the first preform material by heat treatment to increase the material's hardness. The crystalline phase content is, for example, less than 60%, preferably less than 40%, more preferably less than 30%, and even more preferably less than 5%, the percentages being expressed by volume of material.

[0054] In exploratory tests, pellets with a diameter of 10 mm and a thickness of 3 mm showed an increase in hardness of approximately 10% after being heat-treated under vacuum for 40 min at a temperature of 370°C, then rapidly cooled at over 100°C / min. The pellets after heat treatment had a crystalline phase volume fraction of approximately 40%.

[0055] In a second step E2, the first preform is thermoformed, notably by hot drawing without a die under a controlled atmosphere, or under vacuum, or in air, to obtain a second preform. Preferably, in this thermoforming process, 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 exceeding the critical diameter (De) of the amorphous alloy (constituting the second preform) by a factor greater than 5, preferably greater than 10, 100, or 1000. Preferably, the second preform is a rod, bar, or wire, notably with a round cross-section and: a diameter greater than 1 mm, preferably greater than 2 mm, and a length greater than 0.5 m, preferably greater than 1 m or greater than 2 m. In another embodiment, this second step E2 includes hot drawing under a controlled atmosphere, or even under vacuum, to protect the solid metallic glass against oxidation.

[0056] In one execution mode, in the second step E2, a fourth sub-step E21 of heat treatment is carried out in which a partial crystallization of the second preform is carried out before a third machining step E3 in order to increase the hardness of the second preform.

[0057] In a third step E3, the second preform is machined using a force-requiring process, i.e., it is machined by chip removal or abrasion, for example, by grinding. The machining step E3 may include a substep E31 for turning.

[0058] The third step E3 may also include, possibly after substep E31, a substep E33 for rolling the preform in order to: to achieve dimensional tolerances, and / or to improve the surface condition of the pivots in the case of an axis.

[0059] The third step E3 may also include, possibly after substep E31 and / or before substep E33, an additional substep E32 of cutting a tooth, for example cutting a tooth of an exhaust pinion.

[0060] The third step E3 can optionally precede a step E4 of hardening the preform by a partial crystallization heat treatment, possibly after sub-step E31 and / or after sub-step E32 and / or after sub-step E33.

[0061] In a fifth step E5, a finishing step is carried out, in particular a tribofinishing step is carried out on the preform to remove burrs and ensure an optimal surface condition of the finished watch component.

[0062] In one embodiment, a sixth additional step E6 performs surface hardening on the component produced in the third step E3, or on the watch component produced in the fourth step E4, or in the fifth step E5. This surface hardening can be achieved, for example, through thermochemical treatment or ion implantation. In one embodiment, the tribofinishing step may precede the surface hardening.

[0063] Regardless of the method of execution or variant, the implementation process may include: a) in the first step E1, a third substep E13 of sheathing the first preform in a material having a viscosity comparable to the metallic alloy of the first preform at the drawing temperature, for example by means of a polymer sheath (for example a PEI (polyetherimide) on a platinum-based metallic glass preform such as Pt 57.5 Cu 14.7 Ni 5.3 P 22.5) or by means of a mineral glass sheath (for example a phosphate glass on a palladium-based metallic glass preform, b) in the second step E2, drawing the first bi-material (sheathed) preform, and c) in the third step E3, a fifth substep E30 of removing the sheath, for example by dissolution, chemical etching or machining, in order to release the metallic part. For example, a PEI sheath can be dissolved in a solution of N-Methyl-2-Pyrrolidone.

[0064] Regardless of the execution method or variant, the manufacturing process may include, between the second step E2 and the third step E3, an additional grinding step E60, for example centerless grinding, of the second preform to produce a modified preform. In particular, the modified preform has a round cross-section with a diameter within the tolerances required for precision machining, typically h6 on the diameter (+0 µm -6 µm for a diameter of 2 mm).

[0065] Regardless of the embodiment or variant, the manufacturing process may include, after step E2 or after step E60, an additional cold drawing step E70 through a die to obtain a narrower diameter tolerance range of +0 µm to -3 µm, to form a further modified preform. During this operation, the cross-sectional reduction is less than 20%, preferably less than 10%, and more preferably less than 5%. In one embodiment, in this step E70, the second or modified preform is drawn through a die with a profile shape, for example, a toothed shape.

[0066] The process according to the invention relates to the production of a watch component, in particular a watch arbor. Before the end of the process, the partially produced watch component is referred to as the "preform". In particular, at the end of the first step E1, the partially produced watch component is referred to as the "first preform" and, at the end of the second step E2, the partially produced watch component is referred to as the "second preform".

[0067] In the figures, the steps and sub-steps represented by dotted rectangles are optional steps.

Claims

1. Method for making a watch component (100) in amorphous metal alloy, the manufacturing process comprising: - a step (E1) of making a first preform in amorphous metal alloy, then - a step (E2) of hot drawing of the first preform to obtain a second preform, then - a step (E3) of machining of the second preform.

2. Method according to claim 1, characterized in that The amorphous metallic alloy has a supercooling range ΔTx = Tx-Tg greater than 40°C or greater than 60°C or greater than 100°C, Tx being the crystallization temperature and Tg being the glass transition temperature.

3. A method according to any one of the preceding claims, characterized in that The amorphous metallic alloy is a Pd-based, Pt-based, or Zr-based alloy, for example the following compositions given in atomic percentages: - Pd 43 Neither 10 Cu 27 P 20 , - Pt 57.5 Cu 14.7 Neither5.3 P 22.5 - Pd 75 If 15 Ag3Cu7, and - Zr 41.2 Ti 13.8 Cu 12.5 Neither 10 Be 22.5 .

4. A method according to any one of the preceding claims, characterized in that The first step (E1) includes a sub-step (E1.1) of structuring the first preform, in particular by machining or stamping.

5. A method according to any one of the preceding claims, characterized in that the first step (E1) includes a substep (E12) of hardening the material of the first preform by a heat treatment of crystallization, in particular partial crystallization.

6. A method according to any one of the preceding claims, characterized in thatthe second step (E2) includes hot drawing, in particular at a temperature between the glass transition temperature and the crystallization temperature, without a die to obtain the second preform with at least one dimension of the second preform exceeding the critical diameter of the amorphous metallic alloy by a factor greater than 5 or by a factor greater than 10 or by a factor greater than 100 or by a factor greater than 1000.

7. A method according to any one of the preceding claims, characterized in that the second preform is a rod or bar or wire, especially with a circular cross-section, with: - a 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.

8. A method according to any one of the preceding claims, characterized in thatThe step (E1) of making the first preform in amorphous metal alloy includes a sheathing (E13) of the amorphous metal alloy by a thermoplastic material, such as, for example, a polymer or a mineral glass.

9. Method according to the preceding claim, characterized in that the machining step (E3) includes a substep (E30) of removing the sheathing, for example by dissolution, by chemical attack or by machining.

10. A method according to any one of the preceding claims, characterized in that the hot drawing step (E2) includes a substep (E21) of hardening by a partial crystallization heat treatment.

11. A method according to any one of the preceding claims, characterized in that the process further includes, between the hot drawing step (E2) and the machining step (E3), an additional shaping step comprising: - a grinding substep (E60), and / or - a drawing substep through a die (E70).

12. A method according to any one of the preceding claims, characterized in that the machining step (E3) includes machining with application of a force, in particular turning (E31).

13. A method according to any one of the preceding claims, characterized in that the machining step (E3) includes a rolling step (E32).

14. A method according to any one of the preceding claims, characterized in that the machining step (E3) includes a gear cutting (E33) of a tooth, for example a gear cutting.

15. A method according to any one of the preceding claims, characterized in that the process includes, after the machining step (E3), a hardening step (E4) by a partial crystallization heat treatment.

16. Method according to the preceding claim, characterized in that the process includes, after the hardening step (E4), a finishing step (E5), in particular by tribofinishing.

17. A method according to any one of the preceding claims, characterized in thatthe process includes, after the machining step (E3), a finishing step (E5), for example a tribofinishing step.

18. A method according to any one of the preceding claims, characterized in that the process includes a preliminary step (E0) of manufacturing a pre-alloy of the amorphous or partially amorphous alloy, for example by vacuum induction melting (Vacuum Induction Melting VIM) or by arc melting (arc-melter).

19. Watchmaking component (100), in particular axis (100) of a regulating system (200) for a watch part (400), such as a balance staff or an anchor rod or a mobile pinion, obtained by implementing the process according to one of the preceding claims.

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