METHOD FOR MANUFACTURING OR MODIFYING AN ENDODONTIC INSTRUMENT OF NITI ALLOY

Abstract

The invention relates to a method for manufacturing or modifying an endodontic instrument made from an NiTi alloy, comprising a heat-treatment. The invention further relates to an endodontic instrument, preferably obtained by the method, having superior properties with regard to cyclic fatigue resilience.

Claims

1-11. (canceled)

12. An endodontic instrument made of a titanium alloy with a phase transition temperature of at least 37 C., measured according to a bend and free recovery test method based on ASTM F2082/F2082M.

13. The endodontic instrument according to claim 12, wherein the phase transition temperature is at least 40 C.

14. The endodontic instrument according to claim 12, wherein the phase transition temperature is between 45 C. and 70 C.

15. The endodontic instrument according to claim 12, wherein the endodontic instrument has pseudo-plastic behaviour at 25 C.

16. The endodontic instrument according to claim 12, wherein the endodontic instrument has super-elastic behaviour at temperatures above the endodontic instrument's phase transition temperature.

17. The endodontic instrument according to claim 12, wherein the alloy is a shape memory alloy.

18. The endodontic instrument according to claim 12, wherein the alloy is selected from the group consisting of: alpha-titanium alloys, beta-titanium alloys, and nickel-titanium alloys.

19. The endodontic instrument according to claim 12, wherein the endodontic instrument in an unloaded state is substantially linear.

20. The endodontic instrument according to claim 12, wherein a working portion of the endodontic instrument has no bend shape, curve shape or spiral shape in an unloaded state.

21. The endodontic instrument according to claim 12, wherein the endodontic instrument has a mean number of cycles of failure of at least 4000.

22. The endodontic instrument according to claim 12, wherein the endodontic instrument has a mean number of cycles of failure of at least 4300.

23. The endodontic instrument according to claim 12, wherein the endodontic instrument has a mean number of cycles of failure of at least 4500.

24. The endodontic instrument according to claim 20, wherein the mean number of cycles of failure is measured by rotating the samples in a curved groove carved out from a stainless steel block and covered with a glass plate, until breakage of the sample, wherein the groove has a breadth b of 1.5 mm, a depth d of 2 mm, a total length L.sub.1+B+L.sub.2 of 2.1 cm, with L.sub.1 being 10.5 mm and L.sub.2 being 3 mm, and a curvature over and arc length B of 60 with a curvature radius R of 8.25 mm.

25. The endodontic instrument according to claim 21, wherein the mean number of cycles of failure is measured by rotating the samples in a curved groove carved out from a stainless steel block and covered with a glass plate, until breakage of the sample, wherein the groove has a breadth b of 1.5 mm, a depth d of 2 mm, a total length L.sub.1+B+L.sub.2 of 2.1 cm, with L.sub.1 being 10.5 mm and L.sub.2 being 3 mm, and a curvature over and arc length B of 60 with a curvature radius R of 8.25 mm.

26. The endodontic instrument according to claim 22, wherein the mean number of cycles of failure is measured by rotating the samples in a curved groove carved out from a stainless steel block and covered with a glass plate, until breakage of the sample, wherein the groove has a breadth b of 1.5 mm, a depth d of 2 mm, a total length L.sub.1+B+L.sub.2 of 2.1 cm, with L.sub.1 being 10.5 mm and L.sub.2 being 3 mm, and a curvature over and arc length B of 60 with a curvature radius R of 8.25 mm.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0037] Shown is in

[0038] FIG. 1: profile of temperature over time in a simple treatment of files 500C_75 min;

[0039] FIG. 2: profile of temperature over time in a simple treatment of files 500_300, under controlled cooling;

[0040] FIG. 3: profile of temperature over time in a treatment at a first and a second temperature range 575_500_300, under controlled cooling;

[0041] FIG. 4a: front view of a measurement setup of the cyclic fatigue testing groove;

[0042] FIG. 4b: top view on the measurement canal setup of the cyclic fatigue testing groove;

[0043] FIG. 5: results of the cyclic fatigue test (Example 1);

[0044] FIG. 6: DSC diagram of untreated NiTi-control wires;

[0045] FIG. 7: DSC diagram of NiTi wires subject to a simple treatment (600 C. for 1 hr);

[0046] FIG. 8: DSC diagram of NiTi wires subject to a temperature treatment at a first and a second temperature range (600 C. for 1 hr and subsequent exposure to 500 C. for 3.5 hrs, cooling to 300 over 2 hrs);

[0047] FIG. 9: profile of temperature over time in a treatment of a second batch of files at a first and a second temperature range 575_500_300 long;

[0048] FIG. 10: profile of temperature over time in a simple treatment of files of a second batch 500C_300_long;

[0049] FIG. 11: results of the cyclic fatigue test of the files from the second batch (Example 2);

[0050] FIG. 12: results of the tensile stress.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

Example 1

[0051] 60 HyFlex CM Files by Coltene (size/taper 30/0.04) of NiTi-alloy having super-elastic properties were provided. The files had a working portion extending from a distal end of the shank along around an axial length of the shank provided with at least one cutting blade in a spiral shape. The files were manufactured by grinding. Manufacturing included an extent of cold working but might also include annealing steps.

[0052] Ensembles of 10 files each were placed in titanium containers (grade 1). Two of the titanium containers (i.e. 20 files) were placed in a quartz holder and covered by a getter material. The three quartz holders were subsequently and individually put into a vacuum-furnace for treatment as shown in FIGS. 1 to 3. Pressure in the furnace was reduced to 3*10.sup.3 bar and the samples set under a 0.21/min stream of argon gas.

[0053] Twenty files 500C_75 min were kept at 500 C. for 75 min; 10 of them were quenched in water immediately after heat treatment, 10 of them were cooled in ambient air (FIG. 1).

[0054] Twenty files 500_300 were kept at 500 C. for 4 hrs and allowed to cool down to 300 C. over 2 hrs at a constant cooling rate of 1.7 C./min; 10 of them were quenched in water immediately after the heat treatment, 10 of them were cooled at ambient air (FIG. 2).

[0055] Twenty files 575_500_300 were kept at 575 C. for 45 min, allowed to cool down to 500 C. over 15 min, kept at 500 C. for 4 hrs and allowed to cool down to 300 C. over 2 hrs at a constant cooling rate of 1.7 C./min; 10 of the files were quenched in water immediately after the heat treatment, 10 of them were cooled at ambient air (FIG. 3).

[0056] Cyclic fatigue was measured by rotating the samples in a curved groove carved out from a stainless steel block and covered with a glass plate, until breakage of the sample. The groove had a breadth b of 1.5 mm, a depth d of 2 mm, a total length L.sub.1+B+L.sub.2 of 2.1 cm, with L.sub.1 being 10.5 mm and L.sub.2 being 3 mm, and a curvature over and arc length B of 60 with a curvature radius R of 8.25 mm. FIG. 4a is a schematic front view of the stainless steel block 1 with the curved out groove 3. The glass plate is not shown in FIG. 4a. FIG. 4b is a top view of the stainless steel block 1 having a groove 3 with dimensions b and d. The glass plate 2 is mounted to cover the entire extension of the groove 3 carved out of the stainless steel block. The files were mounted to an endo motor and introduced to a maximal extent into the stainless steel groove, covered with the glass plate whilst not touching the canal's front end. Testing was performed at 20 C. and at a rotational speed of 500 rpm. The number of rotations was counted by optical means (monitoring through the glass plate 2 which laterally closes off the stainless steel groove).

[0057] As can be seen from FIG. 5, the files having undergone simple treatment at 500 during only 75 min (500C_75 min) performed poorly in the cyclic fatigues test with a mean 444 cycles to failure (quenching in water; 500C_75 min W) or a mean 446 cycles to failure (cooling at ambient air; 500C_75 min A). The files having undergone simple treatment at 500 C. for 4 hrs with controlled cooling to 300 C. (500_300) performed considerably better, with a mean 3583 cycles to failure (quenching in water; 500_300 W) or a mean 3634 cycles to failure (cooling at ambient air; 500_300_A)

[0058] However, the files having undergone combined heat-treatment at a first and a second temperature range (575_500_300) performed clearly better. The samples quenched in water failed after a mean 5315 cycles (575_500_300_W). The samples quenched in the air failed after a mean 5450 cycles (575_500_300_A). This amounts to an improvement of the resistance to cyclic fatigue by at least 48%, calculated from the cyclic fatigue values of the best comparative group (500_300 quenched in water/air respectively). The quenching in ambient air generally improved performance of the files in cyclic fatigue tests as compared to the files which were quenched in water.

[0059] The drastic improvement of resistance to cyclic fatigue of files 575_500_300 cannot be explained by mere stress relieve over time in the heat treatment. The effect may be a result of the combined effects of precipitation of Ni-rich Ni.sub.4Ti.sub.3 of reduction of microstructural defects and of homogenized microstructure. Thermal characterisation of NiTi-wires by differential scanning calorimetry (DSC) confirms that the heat-treatment impacts phase transition temperature of the alloy. The untreated alloy is austenitic/superelastic at room temperature (FIG. 6). A NiTi-alloy which was subject to 600 C. for 60 min shows more distinct phase 1 transition peaks which occur, however, at relatively low temperatures (FIG. 7). In contrast, a NiTi-alloy which was subject to heat-treatment at a first and a second temperature range according to the invention (600 C. for 1 hr and subsequent exposure to 500 C. for 3.5 hrs, cooling to 300 over 2 hrs) shows clearly defined peaks and a more substantial shift of phase transformation temperatures to values around 60 C. (austenitic transformation) and 20 C. (martensitic transformation; FIG. 8)

[0060] It shall be noted that the DSC measurements merely indicate the effect of the heat treatment on the phase transition behaviour of the alloy. For the purposes of this invention, superelasticity and pseudo-plasticity of the endodontic instrument are characterized by the bend and free recovery principle.

Example 2

[0061] A second batch of 20 pieces of HyFlex CM Files by Coltene (size/taper 30/0.04) of NiTi-alloy with super-elastic properties was provided. As in the previous example, the files had a working portion extending from a distal end of the shank along around an axial length of the shank provided with at least one cutting blade in a spiral shape. The files were manufactured by grinding. Manufacturing included an extent of cold working but might also include annealing steps.

[0062] Ensembles of 10 files each were placed in two titanium containers (grade 1). The titanium containers were placed in a quartz holder and covered by a getter material (grade 1). The quartz holders were subsequently and individually put into a vacuum-furnace for treatment as shown in FIGS. 6 and 7. Pressure in the furnace was reduced to 3*10.sup.3 bar and the samples set under a 0.2 1/min stream of argon gas.

[0063] Ten files 575_500_300 long were kept at 575 C. for 45 min, allowed to cool down to 500 C. over 15 min, kept at 500 C. for 4 hrs and allowed to cool down to 300 C. over 2 hrs at a constant cooling rate of 1.7 C./min; they were quenched in water immediately after the heat treatment, while still located in the titanium containers. The temperature is plotted over time in FIG. 9.

[0064] Ten files 500_300_long were kept at 500 C. for 5 hrs and allowed to cool down to 300 C. over 2 hrs at a constant cooling rate of 1.7 C./min; they were quenched in water immediately after the heat treatment, while still located in the titanium containers. The temperature is plotted over time in FIG. 10.

[0065] Cyclic fatigue was measured by rotating the samples in a canal formed of stainless steel until breakage as indicated above for Example 1.

[0066] As can be seen from FIG. 11, the files having undergone simple treatment at 500 C. for 5 hrs with controlled cooling to 300 C. (500_300 long) performed moderately, with a mean 2908 cycles to failure. In contrast, the files undergone combined heat-treatment at a first and a second temperature range (575_500_300 long) performed clearly better. The samples failed after a mean 4567 cycles. This amounts to an improvement of the resistance to cyclic fatigue by at least 55%, calculated from the cyclic fatigue values of the comparative group (500_300_long).

[0067] In order to complement the characterization of the modified alloy, uni-axial tensile tests were performed. Therefore, 9 pseudo-elastic NiTi wires of 120 mm were examined for tension resistance.

[0068] Sets of 3 wires each were heat treated in a furnace at [0069] 500 C. for 4 hrs (including rapid heating from room temperature to target temperature over 30 min), and subsequent cooling to 300 C. over 2 hrs (000_000_N); [0070] 600 C. for 1 hr (600 060 V); [0071] 575 C. for 45 min, subsequent cooling to 500 C. over 15 min, keeping the wires at 500 C. for 4 hrs, subsequent cooling to 300 C. over 2 hrs (575_conti_N);

[0072] Inert atmosphere (Ar-stream) was maintained only during the initial treatment (if any) at elevated temperatures of 570 C. and above. After removal of the wires from the furnace, they were left for cooling at ambient air.

[0073] The tensile test was performed based on ASTM F2616, with drawing speed settings being adapted to values recommended in publications of SFB 459 (Sonderforschungsbereich der Ruhr-Universitt Bochum).

[0074] The results of the uni-axial tensile test are shown in FIG. 12. As can be seen from the plot, a reference wire having undergone treatment of 500 C. for 4 hrs and cooling to 300 over 2 hrs (000_000_N) remains stiff at ambient temperatures. In contrast, the sets of samples that were subject to heat treatment at elevated temperatures reached elongation of 80% and more before slipping/rupture of the sample. The samples subject to high temperature treatment only (600 C. for 1 hr; 600_060_V, dashed line) can compensate for mechanical strain to some extent by deformation. However, the sample subject to high temperature treatment (at 575 C. for 45 min) and where this treatment is followed by more moderate heat-treatment at 500 C. for 3.5 hrs (controlled cooling to 300 over 2 hrs; 575_conti_N, dotted line) could compensate best for mechanical strain by deformation.

[0075] It can be concluded that only materials that were subject to a combined heat-treatment in steps at distinct temperature ranges provide an optimal balance between homogeneity of microstructure and tensile strength of the material, therefore allowing good resistance to cyclic fatigue, resistance to crack initiation/propagation and satisfactory compensation for mechanical load.