SPIRAL SPRING FOR A HOROLOGICAL MOVEMENT

Abstract

A spiral spring intended to equip a balance of a horological movement, wherein the spiral spring is made of an alloy consisting of Nb, Ti and at least one element selected from Zr and Hf, optionally at least one element selected from W and Mo, possible traces of other elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al, with the following weight percentages: a content of Nb comprised between 40 and 84%, a total content of Ti, Zr and Hf comprised between 16 and 55%, a content for W and Mo respectively comprised between 0 and 2.5%, a content for each of said elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al comprised between 0 and 1600 ppm with the sum of said traces less than or equal to 0.3% by weight. The method for manufacturing the spiral spring is also disclosed.

Claims

1. A spiral spring intended to equip a balance of a horological movement, wherein the spiral spring is made of an alloy consisting of: Nb, Ti and at least one element selected from Zr and Hf, optionally at least one element selected from W and Mo, possible traces of other elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al, with the following weight percentages: a content of Nb comprised between 40 and 84%, a total content of Ti, Zr and Hf comprised between 16 and 55%, a content for W and Mo respectively comprised between 0 and 2.5%, a content for each of said elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al comprised between 0 and 1600 ppm with the sum of said traces less than or equal to 0.3% by weight.

2. The spiral spring according to claim 1, wherein the Nb content is greater than 45% by weight.

3. The spiral spring according to claim 1, wherein the Ti content is greater than or equal to 15% by weight.

4. The spiral spring according to claim 1, wherein the sum of the content of Zr and Hf is comprised between 1 and 40% by weight.

5. The spiral spring according to claim 1, wherein the sum of the content of Zr and Hf is comprised between 5 and 25% by weight.

6. The spiral spring according to claim 1, wherein the sum of the content of Zr and Hf is comprised between 10 and 25% by weight.

7. The spiral spring according to claim 1, wherein the sum of the content of Zr and Hf is comprised between 15 and 25% by weight.

8. The spiral spring according to claim 1, wherein it includes at least 5% by weight of Zr.

9. The spiral spring according to claim 1, wherein it includes Zr and Hf

10. The spiral spring according to claim 1, having a microstructure including Nb in the beta phase and Ti as well as Zr and/or Hf in the alpha phase.

11. The spiral spring according to claim 1, wherein it has an elastic limit greater than or equal to 500 MPa, and a modulus of elasticity greater than or equal to 100 GPa.

12. A method for manufacturing a spiral spring intended to equip a balance of a horological movement, wherein said method successively comprises: a step of provision of a blank from an at least ternary alloy consisting of: Nb, Ti and at least one element selected from Zr and Hf, optionally at least one element selected from W and Mo, possible traces of other elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al, with the following weight percentages: a content of Nb comprised between 40 and 84%, a total content of Ti, Zr and Hf comprised between 16 and 55%, a content for W and Mo respectively comprised between 0 and 2.5%, a content for each of said elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al comprised between 0 and 1600 ppm with the sum of said traces less than or equal to 0.3% by weight, a step of beta type quenching of said blank, so that titanium of said alloy is essentially in the form of a solid solution with niobium in the beta phase, zirconium and/or hafnium also being essentially in the form of a solution solid, a step of application to said alloy of a succession of deformation sequences followed by an intermediate heat treatment, a winding step to form the spiral spring, a final heat treatment step.

13. The method for manufacturing a spiral spring according to claim 12, wherein the beta type quenching is a dissolution treatment, with a duration comprised between 5 minutes and 2 hours at a temperature comprised between 700° C. and 1000° C., under vacuum, followed by cooling under gas.

14. The method for manufacturing a spiral spring according to claim 12, wherein the beta type quenching is a dissolution treatment lasting 1 hour at 800° C. under vacuum, followed by cooling under gas.

15. The method for manufacturing a spiral spring according to claim 12, wherein the final heat treatment as well as the intermediate heat treatment of each sequence is a precipitation treatment of Ti and of Zr and/or Hf in the alpha phase with a duration comprised between 1 hour and 200 hours at a holding temperature comprised between 300° C. and 700° C.

16. The method for manufacturing a spiral spring according to claim 12, wherein the final heat treatment is carried out at a holding temperature comprised between 400° C. and 600° C. for a duration comprised between 4 and 8 hours.

17. The method for manufacturing a spiral spring according to claim 12, wherein, after the step of providing the alloy blank, and before the step of applying a succession of sequences, 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 is added to the blank to facilitate shaping into a wire shape and wherein , before or after the winding step, said wire is stripped of its layer of said ductile material by chemical attack.

Description

DETAILED DESCRIPTION

[0041] The invention relates to a watch spiral spring made of an at least ternary alloy including niobium and titanium and one or more additional elements.

[0042] According to the invention, this alloy consists of: [0043] Nb, Ti and at least one element selected from Zr and Hf, [0044] optionally at least one element selected from W and Mo, [0045] possible traces of other elements selected from O, H, C, Ta, Fe, N, Ni, Si, Cu, Al, with the following weight percentages: [0046] a content of Nb comprised between 40 and 84%, [0047] a total content of Ti, Zr and Hf comprised between 16 and 55%, [0048] a content for W and Mo respectively comprised between 0 and 2.5%, [0049] a content for each of said elements selected from O, H, C, Ta, Fe, N, Ni, Si, Cu, Al comprised between 0 and 1600 ppm with the sum of said traces less than or equal to 0.3% by weight.

[0050] Preferably, the content by weight of Nb is greater than 45%, or even greater than or equal to 50%, in order to obtain a sufficient percentage of beta phase having a strongly positive TEC intended to be compensated by the negative TEC of the alpha phase of Ti, Zr, Hf.

[0051] Preferably, the content by weight of Ti is maintained at a minimum content of 15% because Ti is more economical than Zr and Hf. Furthermore, it has the advantage of having a lower melting temperature than Zr and Hf, which facilitates casting.

[0052] 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.

[0053] 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.

[0054] 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.

[0055] The percentage by weight of tantalum is less than or equal to 0.10% by weight of the total.

[0056] 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.

[0057] 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.

[0058] The percentage by weight of nickel is less than or equal to 0.01% of the total.

[0059] The percentage by weight of silicon is less than or equal to 0.01% of the total.

[0060] 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.

[0061] The percentage by weight of aluminium is less than or equal to 0.01% of the total.

[0062] According to the invention, Ti is partly replaced by Zr and/or Hf forming, like Ti, alpha precipitates, so as to accelerate the precipitation during the fixing and therefore to reduce the production times. Advantageously, the sum of the Zr and Hf content is comprised between 1 and 40% by weight. Preferably, the sum of the Zr and Hf content is comprised between 5 and 25%, more preferably between 10 and 25% and even more preferably between 15 and 25% by weight.

[0063] Advantageously, Ti is at least replaced by Zr which also allows to reduce the secondary error which is a measurement of the curvature of the rate which is generally approximated by a straight line passing through two points (8° C. and 38° C.). Tests were carried out on binary alloys Nb-Ti with a weight percentage of Ti of 47% (NbTi47) and Nb-Zr with weight percentages of Zr comprised between 0 and 70% to show the effect of Ti and Zr respectively on the secondary error. The secondary error is measured at 23° C. This is the difference in rate at 23° C. relative to the straight line linking the rate at 8° C. to that at 38° C. For example, the rate at 8° C., 23° C. and 38° C. can be measured using a Witschi chronoscope-type apparatus.

[0064] Table 1 below shows the data for pure Nb, the NbTi47 alloy and the Nb-Zr alloy as a function of the percentage by weight of Zr. Pure Nb has a secondary error at 23° C. of -6.6 s/d. The precipitation of Ti in the NbTi47 alloy compensates for the negative effect of Nb with however an excessive rise with a positive value reaching 4.5 s/d. Nb-Zr alloys, on the other hand, have a negative secondary error for a Zr content greater than 0%, or even zero for Zr contents greater than or equal to 45% by weight. It follows that the partial replacement of Ti by Zr in a ternary alloy allows to compensate for the too positive effect of Ti on the secondary error. Adding a few percent by weight of Zr already allows to reduce the secondary error to a value closer to 0 than for the binary NbTi47 alloy. Thus, advantageously, the Zr content is at least 5% by weight.

TABLE-US-00001 TABLE 1 Alloy % wt Secondary error at 23° C. Pure Niobium  0% −6.6 s/d NbTi47 47% 4.5 s/d Nb.sub.30Zr.sub.70 70% −0.2 s/d Nb.sub.45Zr.sub.55 55% 0.0 s/d Nb.sub.50Zr.sub.50 50% 0.2 s/d Nb.sub.55Zr.sub.45 45% 0.0 s/d Nb.sub.60Zr.sub.40 40% −3.0 s/d Nb.sub.65Zr.sub.35 35% −4.1 s/d Nb.sub.70Zr.sub.30 30% −4.8 s/d Nb.sub.80Zr.sub.20 20% −5.0 s/d Nb.sub.85Zr.sub.15 15% −5.8 s/d Nb.sub.90Zr.sub.10 10% −6.0 s/d Nb.sub.100  0% −6.6 s/d

[0065] The alloy may further include W and Mo in a content by weight for each comprised between 0 and 2.5% in order to increase the Young's modulus of the alloy, which allows for a given torque of the spring to reduce the thickness of the spiral and thereby lighten the spiral.

[0066] Advantageously, the spiral spring according to the invention has a multiphase microstructure including niobium in centred cubic beta phase, and a single alpha phase of titanium and zirconium and/or hafnium.

[0067] To obtain such a microstructure, it is necessary to finalise the precipitation in the alpha phase by heat treatment during the fixing of the spring in the manufacturing method successively implementing the following steps: [0068] a step of provision or production of a blank. For example, the blank can be made by melting the elements in an electric arc or electron gun furnace to form a billet or ingot which is hot forged then cold deformed and heat treated between the deformation phases. The blank is made of an at least ternary alloy consisting of: [0069] Nb, Ti and at least one element selected from Zr and Hf, [0070] optionally at least one element selected from W and Mo, [0071] possible traces of other elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al, with the following weight percentages: [0072] a content of Nb comprised between 40 and 84%, [0073] a total content of Ti, Zr and Hf comprised between 16 and 55%, [0074] a content for W and Mo respectively comprised between 0 and 2.5%, [0075] a content for each of said elements selected from O, H, Ta, C, Fe, N, Ni, Si, Cu, Al comprised between 0 and 1600 ppm with the sum of said traces less than or equal to 0.3% by weight, [0076] a step of beta type quenching of said blank, so that titanium of said alloy is essentially in the form of a solid solution with niobium in the beta phase, zirconium and/or hafnium also being essentially in the form of a solid solution, [0077] a step of application to said alloy of a succession of deformation sequences followed by an intermediate heat treatment. Deformation means a deformation by drawing and/or rolling. Drawing may require the use of one or more dies during the same sequence or during different sequences if necessary. Drawing is carried out until a wire with a round section is obtained. Rolling can be done in the same deformation sequence as drawing or in another sequence. Advantageously, the last sequence applied to the alloy is a rolling preferably with a rectangular profile compatible with the entry section of a winding pin. [0078] a winding step to form the spiral spring, [0079] a final heat treatment step.

[0080] In these coupled deformation-heat treatment sequences, each deformation is carried out with a given deformation amount comprised between 1 and 5, this deformation amount corresponding to the conventional formula 21n(d0/d), wherein d0 is the diameter of the last beta quenching, and where d is the diameter of the cold-worked wire. The global accumulation of the deformations on the whole of this succession of sequences brings a total deformation amount comprised between 1 and 14.

[0081] Each coupled deformation-heat treatment sequence includes, each time, a heat treatment of precipitation of the Ti, Zr and/or Hf alpha phase.

[0082] The beta quenching prior to the deformation and heat treatment sequences is a dissolution treatment, with a duration comprised between 5 minutes and 2 hours at a temperature comprised between 700° C. and 1000° C., under vacuum, followed by cooling under gas.

[0083] Even more particularly, this beta quenching is a dissolution treatment, lasting 1 hour at 800° C. under vacuum, followed by cooling under gas.

[0084] To return to the coupled deformation-heat treatment sequences, the heat treatment is a precipitation treatment with a duration comprised between 1 hour and 200 hours at a temperature comprised between 300° C. and 700° C. More particularly, the duration is comprised between 3 hours and 30 hours at a temperature comprised between 400° C. and 600° C.

[0085] More particularly, the method includes between one and five coupled deformation-heat treatment sequences.

[0086] More particularly, the first coupled deformation-heat treatment sequence includes a first deformation with at least 30% reduction in section.

[0087] More particularly, each coupled deformation-heat treatment sequence, other than the first, includes one deformation between two heat treatments with at least 25% reduction in section.

[0088] More particularly, after this production of said alloy blank, and before the deformation-heat treatment sequences, in an additional step, 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 is added to the blank to facilitate shaping into a wire shape during deformation. And, after the deformation-heat treatment sequences or after the winding step, the wire is stripped of its layer of ductile material, in particular by chemical attack.

[0089] Alternatively, the surface layer of ductile material is deposited so as to form a spiral spring whose pitch is not a multiple of the thickness of the blade. In another variant, the surface layer of ductile material is deposited so as to form a spring whose pitch is variable.

[0090] In a particular horological application, ductile material or copper is thus added at a given moment to facilitate shaping into a wire shape, so that a thickness of 10 to 500 micrometres remains on the wire with the final diameter of 0.3 to 1 millimetres. 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 by winding.

[0091] The supply of ductile material or copper can be galvanic, or else mechanical, it is then a jacket or a tube of ductile material or copper which is adjusted on a bar of the alloy with a large diameter, then which is thinned during the steps of deformation of the composite rod.

[0092] The removal of the layer is in particular possible by chemical attack, with a solution based on cyanides or based on acids, for example nitric acid.

[0093] The final heat treatment is carried out for a duration comprised between 1 hour and 200 hours at a temperature comprised between 300° C. and 700° C. More particularly, the duration is comprised between 3 hours and 30 hours at a temperature comprised between 400° C. and 600° C. Advantageously, the duration is comprised between 4 and 8 hours with a hold at a temperature comprised between 400° C. and 600° C. During this final heat treatment, the precipitation of titanium as well as hafnium and/or zirconium in the alpha phase is finalised.

[0094] By a suitable combination of sequences of deformation and heat treatment, it is possible to obtain a very fine microstructure, which is in particular nanometric, including beta niobium and an alpha phase of titanium and hafnium and/or zirconium. This alloy combines a very high elastic limit, greater than at least 500 MPa and a modulus of elasticity greater than or equal to 100 GPa and preferably greater than or equal to 110 GPa. This combination of properties is well suited for a spiral spring. Furthermore, this at least ternary niobium-titanium-hafnium and/or zirconium alloy according to the invention can easily be covered with ductile material or copper, which greatly facilitates its deformation by drawing.

[0095] This alloy also has an effect similar to that of “Elinvar”, with a practically zero thermo-elastic coefficient in the range of temperatures commonly used in watches, and adapted for the manufacture of self-compensating spirals.