Patent Application
20220275495
The present invention relates to low temperature hardening of titanium and other Group IV metals. Specifically, a method of oxygen hardening a Group IV metal is provided as well as a hardened Group IV metal component. The method and the component are useful for any application where hard metals can be used. The component of the invention is especially useful where the aesthetics of the metal is important, e.g. for watches, jewellery, and glasses.
It is well-known that titanium and other Group IV metals can be hardened by interstitial oxygen and that there is a direct correlation between the oxygen content and the hardness, the higher the oxygen content the harder the metal. It is further well-known that oxygen hardening of titanium should be performed at a temperature as low as possible in order to avoid grain growth and general distortion of the material.
Thus, JPH08134625 discloses a method of forming and surface-hardening titanium or titanium alloy sheet. The method employs a forming gas containing CO2 gas, and by performing gas pressure forming, the titanium thin plate can be formed into a predetermined shape, and at the same time a hardened layer is formed. The method is done between 700° C. and 1100° C., although a temperature lower than the β transformation point is preferred. Above 1100° C. excessive oxidising is found.
JPH059703 discloses a surface hardening treatment method of a titanium material. The titanium material is heat treated in an atmosphere containing a CO2 gas, which is reduced and decomposed into oxygen and carbon, so that the surface of the titanium material is hardened by solid solution strengthening with these as interstitial elements. A temperature of 700° C. or more is used and a curing time within 10 hours is preferred.
JPH08104970 discloses a surface hardening treatment of a titanium material, aiming to easily form a thick surface-hardened layer without roughening of the surface. The titanium surface is hardened by heating to a predetermined heating temperature in an atmosphere consisting of a CO2 gas and an inert gas or a nitrogen gas, and then in an inert gas or vacuum. Specifically, oxygen and carbon atoms were found to penetrate into the surface of a titanium material by heating with a specific partial pressure of CO2 gas, and a heat treatment in an inert gas or vacuum caused the oxygen and carbon to diffuse inside, thereby forming a thick hardened layer with small surface roughness. In an example, pure titanium was heated in a mixed gas of CO2 and argon for 3 hours at 800° C. followed by diffusion heat treatment at 850° C. for 3 hours in vacuum.
JPH1192911 aims to cure a titanium member at a temperature which does not cause surface roughness, but forms a Vickers hardness of at least 750 at a depth of 1 μm from the surface without forming a coloured substance on the surface. In the process, the member is heated to 700 to 800° C. and treated in a reduced pressure atmosphere containing a nitrogen component and an oxygen component. Nitrogen monoxide, nitrogen dioxide or nitrous oxide, or ammonia gas can be used as the nitrogen containing component, and water or oxygen can be used as the oxygen containing component. For example, a titanium member can be treated at 0.3 Torr of nitrous oxide at 700-800° C. for 1 to 10 hours.
U.S. Pat. No. 6,221,173 discloses a titanium or titanium alloy having a hard surface layer comprising a first hard layer containing nitrogen in solid solution in a range of 0.6 to 8.0 wt % and oxygen in solid solution in a range of 1.0 to 14.0 wt % and a second hard layer below the first hard layer containing oxygen in solid solution in a range of 0.5 to 14.0 wt %. The hard surface layer can be provided by treating the alloy at 650 to 830° C. in a nitrogen atmosphere with traces of oxygen, water, carbon dioxide or carbon monoxide at a total pressure of 1.33 to 1330 Pa. The length of treatment time is from 1 to 10 hours. Thereby, nitrogen and oxygen diffuse into the interior of the titanium or titanium alloy without forming nitrides and oxides of the titanium.
US 2003/041922 discloses a method of strengthening a titanium alloy to improve wear resistance. The method comprising heating the titanium alloy in an atmosphere of CO2 at 600 to 900° C. to diffuse C and O atoms into the titanium alloy without forming titanium oxide. A preferred temperature range is 800 to 850° C., and in particular at temperatures above 900° C., titanium oxides are formed. The reaction time may be 0.5 to 50 hours.
WO 97/14820 discloses a method of treating titanium parts at atmospheric pressure in a mixture of nitrogen, methanol and optionally natural gas or propane at a temperature between 1450° F. and 1850° F. Thereby a coating is caused to form on the alloy surface consisting predominantly of titanium oxides with regions of oxynitrides and at times some carbonitrides. The part can then be treated in a vacuum furnace at 1200° F. to 1450° F. to reduce the hydrogen level in the parts to improve yield strength.
WO 2008/154593 and WO 2007/078427 disclose medical implants of zirconium having a diffusion hardened zone and optionally also a ceramic zone having a layered structure comprising, and a method of making a surface hardened medical implant. For example, a zirconium niobium alloy sample is oxidised in air at 635° C. followed by treatment in a vacuum furnace.
WO 2017/207794 discloses a case hardened component of a titanium alloy having a diffusion zone comprising oxygen and carbon in solid solution and having a distinct phase of a carbo-oxide compound.
EP 0931848 discloses a decorative hardened titanium material, a method of processing a titanium material, and a method of processing a decorative titanium material. The hardened surface layer including nitrogen and oxygen and has a surface crystal grain size in the range from 0.1 to 60 μm.
WO 99/04055 discloses a method of case hardening an article formed of titanium, zirconium or an alloy of titanium and/or zirconium. The method involves heat-treating the article in an oxidising atmosphere to form an oxide layer followed by heat-treating the article in a vacuum to cause oxygen from the oxide layer to diffuse into the article.
In light of the methods disclosed by the prior art there is still a need for an improved process of hardening titanium or other Group IV metals and their alloys.
In a first aspect, the present invention relates to a method of oxygen hardening a Group IV metal, the method comprising the steps of:
In a second aspect, the present invention relates to a Group IV metal component comprising a material core having a core hardness and a surface hardness of at least the core hardness +200 HV0.025, a diffusion zone having oxygen in solid solution in the range of a level providing a hardness of 120% of the hardness of the material core to the saturation level of the Group IV metal over a thickness from the surface in the range of 10 μm to 100 μm, the diffusion zone further containing carbon and/or nitrogen in solid solution at a concentration showing a local maximum in the diffusion zone of the carbon content and/or the nitrogen content as detectable with Glow Discharge Optical Emission Spectroscopy (GDOES).
The Group IV metal component of the second aspect is obtainable in the method of the first aspect. In particular, the Group IV metal component of the second aspect is obtainable when the oxidising atmosphere comprises a carbon containing molecule or a nitrogen containing molecule, or both a carbon containing molecule and a nitrogen containing molecule.
Any Group IV metal is appropriate for both aspects of the invention. In specific embodiments the Group IV metal is selected from the list of titanium, titanium alloys, zirconium and zirconium alloys. In the context of the invention the component may consist of a Group IV metal, e.g. a titanium alloy, or it may comprise other materials. For example, the component may have a core of another material, a polymer, glass, ceramic or another metal, and an outer layer of the titanium alloy or zirconium. Likewise, a workpiece treated in the method of the invention may also have a core of another material. The outer layer need not completely cover the outer surface of the component. The component may for example be prepared from additive manufacturing or 3D printing prior to be treated in the methods of the invention.
Group IV metals, and their alloys, can be described in terms of their hardness. Group IV metals can be hardened by dissolution of oxygen in the metal, but regardless of any oxygen hardening, the Group IV metal will have a core hardness. Thus, the core hardness corresponds to the hardness, e.g. the surface hardness, of the Group IV metal before hardening. The core hardness generally depends on the specific Group IV metal, but when the Group IV metal has been treated in the method of the invention, the surface hardness will at least 200 HV0.025 units higher than the core hardness. It is preferred that the surface hardness is analysed using load of up to 50 g, i.e. HV0.05, although any value for surface hardness will be HV0.025 unless noted otherwise. Surface hardness values obtained using loads of up to 50 g, e.g. HV0.01, HV0.025 or HV0.005, are considered to be representative also for the HV0.025-value. Grade 2 titanium will typically have a core hardness of about 200 HV0.025, so that Grade 2 titanium hardened according to the invention will have a surface hardness of at least 400 HV0.025. Grade 5 titanium will typically have a core hardness of about 300 HV0.025, so that Grade 5 titanium hardened according to the invention will have a surface hardness of at least 500 HV0.025. However, in general higher surface hardnesses are available from the method of the invention. In a specific embodiment, the surface hardness is at least 650 HV0.025. A surface hardness is at least 650 HV0.025 can be obtained for any Group IV metal. It is preferred that the surface hardness is at least 700 HV0.025, e.g. at least 800 HV0.025.
The method of the invention allows that the workpiece after treatment according to the method regains its metallic lustre so that a component of the invention cannot be differentiated from the workpiece before treatment by visual inspection. Thus, when the workpiece has a mirror polish appearance the mirror polish appearance will also be found on the component after treatment in the method. In the context of the invention, a “mirror polish appearance” is defined as a surface with an arithmetical mean deviation (Ra) roughness of <0.1 μm in accordance with the ISO 1302:2002 standard. For example, the Ra value can be measured using a Taylor-Hubson Surtronic S25 measuring over a length of 1.25 mm. A mirror polish surface may also be referred to as an N3 surface, and the two terms can be used interchangeably. In a preferred embodiment, the workpiece of a Group IV metal is polished prior to oxidising the Group IV metal to provide a surface roughness of <0.1 μm in accordance with the ISO 1302:2002 standard. The surface roughness of <0.1 μm will also be observed for the workpiece after the diffusion step. A mirror polish appearance is generally available for Group IV metals, titanium in particular, but when the workpiece contains aluminium, e.g. Grade 5 titanium, the first temperature should not be higher than 700° C. for the method to provide a mirror polish appearance. However, it is preferred that the Group IV metal does not contain aluminium when a mirror polish appearance is relevant. Furthermore, the oxidising atmosphere should not contain carbon containing molecules, other than CO2, when a mirror polish appearance is relevant. When the gaseous oxidising species is CO2 and the oxidising atmosphere is not supplemented with further carbon containing molecules a commercially pure (CP) titanium, e.g. Grade 2 or Grade 4, can be provided with a surface hardness of at least 1100 HV0.025 while retaining the mirror polish appearance. Thus, the method of the invention provides a titanium component having a mirror polish appearance with a surface hardness of at least 1100 HV0.025. The presence of further carbon containing molecules as unavoidable impurities does not affect the mirror polish appearance.
The present inventors have surprisingly found that if the Group IV metal comprises aluminium as an alloying element, the metallic appearance after treatment will be duller than when a workpiece made from a Group IV metal not comprising aluminium is treated. Without being bound by theory the present inventors believe that aluminium forms thermodynamically more stable oxides than the Group IV metal in the oxidising step thereby preventing that all oxygen is diffused into the Group IV metal in the diffusion step. However, unavoidable impurities of aluminium will not cause problems for the formation of metallic lustre on the Group IV metal. The present inventors have further observed that when aluminium is present, a higher surface hardness is available than when no aluminium is present. In a preferred embodiment, the Group IV metal does not comprise aluminium as an alloying element. In a particularly preferred embodiment, the Group IV metal is a CP Group IV metal, e.g. titanium of the grades 2 and 4, or Zr702 zirconium. In another embodiment, the Group IV metal comprises aluminium, e.g. the Group IV metal may be Grade 5 titanium, which is also known as Ti6Al4V, or Ti6Al4V ELI also known as Grade 23. When the Group IV metal is of CP grade, it is possible to obtain a mirror polish appearance after treatment in the method of the invention. The workpiece treated or the component of the invention may comprise aluminium, e.g. as a section separate from the Group IV metal, while the Group IV metal does not comprise aluminium as an alloying element. In an embodiment of the invention, the component of the invention, e.g. of titanium of grade 2 or 4, has a mirror polish appearance. A mirror polish appearance may not be available when the oxidising atmosphere contains other carbon containing molecules than CO2, since additional carbon, e.g. CO, tends to provide a darker non-stratified oxide layer, which may be reflected in the surface of the final component. It is therefore a preferred embodiment that the oxidising atmosphere does not contain CO. Likewise, a component of the invention having a mirror polish appearance is available using CO2 as the oxidising atmosphere.
The method of the invention in an oxidising step provides a Group IV metal with a layer of Group IV metal, e.g. titanium oxide or zirconium oxide, which serves as a reservoir for oxygen atoms that in the diffusion step are diffused into the Group IV metal to form interstitially dissolved oxygen in the Group IV metal. The oxidising step may also be referred to as the first step. The present inventors have surprisingly found that it is possible to form an intermediary non-stratified oxide layer that is so robust and stably integrated with the Group IV metal that oxygen atoms can be diffused into the Group IV metal to form a superficial diffusion zone comprising oxygen in solid solution. The diffusion takes places in the diffusion step after the oxidising step, and the diffusion step may also be referred to as the second step. Thus, the non-stratified oxide layer will effectively be removed from the surface to be replaced with the diffusion zone, and the Group IV metal will be returned to its apparent metallic state but with a greatly increased surface hardness, i.e. at least 200 HV0.025 units higher than the core hardness, e.g. at least 650 HV0.025, or at least 800 HV0.025, or at least 1000 HV0.025, due to the interstitial oxygen. Even though the oxide layer is removed in the diffusion step, a natural oxide layer will inevitably form on the surface of the hardened Group IV metal. A naturally formed oxide layer will be in the nanometer range and will not change the metallic appearance of the hardened Group IV metal.
The method of the invention uses a gaseous oxidising species. Any gaseous oxidising species that can be brought to a gaseous form may be used in the method. The oxide layer provided in the oxidising step is non-stratified, and the present inventors have found that the first temperature and also the oxidising duration can be chosen based on the oxidising capability of commonly used gaseous oxidising species to provide the non-stratified oxide layer. In the context of the invention, the workpiece with the non-stratified oxide layer may be referred to as the “intermediary workpiece”, and the two terms may be used interchangeably. Stratification of the oxide layer is an indication that the oxide layer has insufficient stability to serve as a reservoir for oxygen atoms for diffusion into the Group IV metal. In general, the oxidising capabilities of CO2, O2 and N2O can be ranked as follows: CO2<O2<N2O. A temperature below 500° C. is too low to form the oxide layer, but an upper temperature limit can be determined for a gaseous oxidising species. Water vapour, i.e. H2O is also contemplated as a gaseous oxidising species. However, when hydrogen containing molecules are present in the oxidising atmosphere, or even in the inert atmosphere, hydrogen will dissolve in the Group IV metal where the presence of interstitial hydrogen will lead to embrittlement of the Group IV metal. Thus, it is preferred that neither the oxidising atmosphere nor the inert atmosphere contains hydrogen containing molecules, in particular H2O.
Regardless of the choice of gaseous oxidising species it is preferred that the first temperature is in the range of 600° C. to 700° C. At a first temperature in the range of 500° C. to 600° C., the oxidising step will generally be undesirably slow, but if the first temperature is at least 600° C. the workpiece will be oxidised at an acceptable rate. When the first temperature is in the range of 700° C. to 800° C., i.e. when possible with regard to the chosen gaseous oxidising species, grain growth may be observed for the Group IV metal, so that when grain growth is unacceptable, the first temperature should be up to 700° C., e.g. in the range of 500° C. to 700° C., or in the range of 600° C. to 700° C.
The oxidising step has an oxidising duration. The oxidising duration is determined by the time the workpiece is treated with the gaseous oxidising species at the first temperature. The workpiece may be heated, e.g. from ambient temperature, to the first temperature before being exposed to the gaseous oxidising species or the workpiece, e.g. at ambient temperature, may be exposed to the gaseous oxidising species being at the first temperature. When the workpiece is heated prior to exposure to the gaseous oxidising species, the workpiece may be heated in an inert atmosphere, in vacuum or in the gaseous oxidising species, it is preferred that the time the workpiece spends in the temperature from 500° C. to the first temperature is minimised.
In general, the thickness of the oxide layer is determined by the oxidising duration, with due consideration of the oxidising capability of the gaseous oxidising species employed. The longer the oxidising duration, the thicker the oxide layer, and in general, dissolution of elements into a Group IV metal is considered to be parabolic so that a doubling of the dissolution depth requires a four times longer reactive duration. The composition of the oxide layer will generally be MeO2, where “Me” is the Group IV Metal, e.g. TiO2, or ZrO2, although trace amounts of other elements, e.g. carbon and/or nitrogen or other metals from alloys of the Group IV metal, may also be present. Therefore, the thickness of the diffusion zone will depend proportionally on the thickness of the oxide layer. A thickness of only 1 μm of the oxide layer is considered sufficient to provide a diffusion zone of a thickness to provide a surface hardness of the core hardness plus at least 200 HV0.025 and a hardness profile over the cross-section to identify the diffusion zone, regardless of the Group IV metal treated in the method. A thickness of the oxide layer of at least 2 μm is considered sufficient to provide a diffusion zone of a thickness to provide a surface hardness of at least 650 HV0.025. However, it is preferred that the oxidising duration is sufficient to provide a thickness of the non-stratified oxide layer in the range of 5 μm to 15 μm. The oxidising duration for providing a non-stratified oxide layer with a thickness in the range of 5 μm to 15 μm can be determined by inspection of the cross-section of intermediary workpieces.
Once the oxide layer is formed, the intermediary workpiece can be stored as long as desired before treating in the diffusion step. The non-stratified oxide layer is so stable that normal handling of the intermediary workpiece will not affect the non-stratified oxide layer. Therefore, the method of the invention is highly flexible since the oxidising step can be performed in a first oven, e.g. an oven without vacuum capabilities, and the transferred to another oven that does have vacuum capabilities. This advantageously allows for logistical optimisation of producing the component of the invention. Moreover, the stability of the non-stratified oxide layer and the intermediary workpiece allows that the conditions of the diffusion step can be selected independently from the choice of oxidising gaseous species employed in the oxidising step.
CO2 as the gaseous oxidising species, being the mildest gaseous oxidising species, allows formation of a stable, non-stratified oxide layer at any temperature at or above 500° C. without regard to the oxidising duration. However, in order to limit deformation and grain growth in the Group IV metal, the upper temperature limit of CO2 is 800° C. For practical reason and in order to limit thickness of the oxide layer the oxidising duration with CO2 may be up to 16 hours, although stable non-stratified oxide layers will also form in longer oxidising durations. For CO2 the oxidising duration is preferably in the range of 1 hour to 16 hours.
N2O is the most capable gaseous oxidising species of commonly used gaseous oxidising species, and N2O has an upper temperature limit of 700° C. Likewise, the non-stratified oxide layer can be formed faster than for CO2, and it is preferred that the oxidising duration is in the range of 10 minutes to 2 hours for N2O. In a certain embodiment, N2O is preferred as the gaseous oxidising species since the first temperature can be lower, e.g. in the range of 500° C. to 650° C., which further decreases the risk of deformation and grain growth in the Group IV metal.
It is also contemplated that O2 may be used as the gaseous oxidising species. However, when O2 is used as the gaseous oxidising species, the diffusion zone will not contain carbon and/or nitrogen in solid solution from the oxidising treatment. O2 has a higher oxidising capability than CO2 and the upper temperature limit is 750° C. The higher oxidising capability of O2 compared to CO2 also limits the oxidising duration. Thus, if the gaseous oxidising species is O2, the oxidising duration is limited to 3 hours in order to prevent formation of a stratified oxide layer. With O2 as the gaseous oxidising species, an oxidising duration of 30 minutes is considered to provide a non-stratified oxide layer of sufficient thickness to provide a surface hardness of at least 1000 HV0.025 after the diffusion step. The oxidising duration for O2 as the gaseous oxidising species is preferably in the range of 30 minutes to 3 hours.
When O2 is used as the oxidising species, the first temperature may be in the range of 500° C. and 750° C. with an oxidising duration in the range of 30 minutes to 3 hours, or the first temperature may be in the range of 600° C. and 650° C. with an oxidising duration in the range of 30 minutes to 2 hours.
It is preferred that the pressure in the oxidising atmosphere is ambient pressure. It is further preferred that the gaseous oxidising species is at ambient pressure, i.e. that the oxidising atmosphere does not contain other molecules. However, it is also contemplated that the oxidising atmosphere may be at ambient pressure and that the partial pressure of the gaseous oxidising species is reduced by the addition of an inert gas, e.g. a noble gas such as argon or helium. Operation at ambient pressure simplifies the process compared to operation at amended, in particular lowered, pressures. When the oxidising atmosphere contains CO, it is preferred that the pressure of the oxidising atmosphere is at ambient pressure.
The oxidising atmosphere may also contain further molecules that can provide atoms for diffusion into the Group IV metal, and which can be integrated in the non-stratified oxide layer. The oxidising atmosphere may for example be ambient air where O2 is the gaseous oxidising species thus being present at about 20% or a partial pressure of about 0.2 atm and is mixed with N2 at about 80% or a partial pressure of about 0.8 atm. The presence of N2 can increase the hardness of the treated workpiece although dissolution of nitrogen atoms from N2 may change the appearance of the surface so that a mirror polish appearance will not be available with N2 is present in the oxidising atmosphere. It is therefore preferred that atmospheric air is not employed, and likewise it is preferred that N2 is not included in the oxidising atmosphere. However, interstitial nitrogen in the component of the invention or a workpiece treated in the method of the invention provides an increased hardness, both of the surface and also the cross-sectional hardness in the diffusion zone.
Oxidising a workpiece of a Group IV metal will increase the volume of the workpiece, due to the inclusion of the oxygen atoms in the oxide layer. Thus, the intermediary workpiece will have a larger volume than the untreated workpiece. However, the inventors have now surprisingly found that when the intermediary workpiece is treated in the diffusion step, the oxygen atoms will diffuse into the Group IV metal and return the component to its original dimensions in the untreated state before the first oxidising step. However, in order to ensure that the component of the invention has the same dimensions as the untreated workpiece, the thickness of the non-stratified oxide layer should be limited to 50 μm, in particular to 25 μm. Thus, the method of the invention allows that a component of a Group IV metal in its final shape is hardened without affecting its shape or dimension. This is especially relevant when grain growth is also undesirable and the first temperature is up to 700° C. The component to be treated is in its final shape. When a mirror polish appearance is intended, the component may be polished to provide a mirror polish appearance before treatment according the method of the invention, i.e. the surface has an Ra roughness of <0.1 μm. The method advantageously allows that the mirror polish appearance is also observed after treatment, i.e. the surface has an Ra roughness of <0.1 μm after treatment.
In the diffusion step oxygen from the non-stratified Group IV metal oxide is diffused into the Group IV metal, and the diffusion step can be performed independently of the parameters employed in the oxidation step. However, in order to prevent further oxidisation of the Group IV metal, the partial pressure of the gaseous oxidising species should be as low as possible. For example, the partial pressure of the gaseous oxidising species may be up to 10−4 mbar, although it is preferably lower, e.g. up to 10−5 mbar or up to 10−6 mbar.
The diffusion step may be performed in a vacuum. In the context of the invention, “vacuum” means that the pressure is up to 10−4 mbar although the composition of the atmosphere is not limited. In another embodiment, the diffusion step is performed in an inert atmosphere. In the context of the invention, an “inert atmosphere” is an atmosphere that does not contain components, except for unavoidable impurities, that will interact with the Group IV metal. A preferred inert atmosphere is a noble gas, e.g. argon. It is preferred to conduct the diffusion step in vacuum since this will more easily ensure that the hardened component retains its metallic lustre after being treated in the method of the invention. The present inventors have surprisingly observed that when the pressure in the diffusion step is above 10−4 mbar contaminants, including gaseous residuals, found in the oven, can prevent reformation of a metallic lustre on the component after treatment in the method of the invention.
The diffusion step is performed at a second temperature in the range of 500° C. to 800° C. over a diffusive duration of at least 0.1 hour, e.g. at least 1 hour. The diffusive duration should be sufficient to allow that the non-stratified oxide layer of the intermediary workpiece will be removed by allowing the oxygen atoms to diffuse into the Group IV metal. The diffusive duration does not have an upper limit. However, if the diffusive duration is extended excessively, the oxygen can eventually be distributed too evenly in the Group IV metal for the Group IV metal to have a diffusion zone providing a sufficient hardness. Thus, the diffusive duration should generally not be longer than 100 hours. The diffusive duration will depend on the thickness of non-stratified oxide layer, and the thicker the non-stratified oxide layer, the longer the diffusive duration for removal of the non-stratified oxide layer. The diffusive duration can therefore be considered to be determined by the choice of gaseous oxidising species, and also the first temperature and the oxidising duration. The diffusive duration is independent on the choice of Group IV metal.
In general, the higher the temperature the faster the diffusion, and since the gaseous oxidising species is not present to oxidise the workpiece the second temperature is less limited than the first temperature. It is therefore possible for the second temperature to be higher than the first temperature. Thus, when the second temperature is higher than the first temperature the hardening can be completed faster. In an embodiment, the second temperature is higher than the first temperature. In a further specific embodiment, the second temperature in the range of 600° C. to 750° C., e.g. 650° C. to 700° C. A second temperature of up to 700° C. can be selected when grain growth is undesirable, since a second temperature of up to 700° C. will prevent grain growth, and also deformation, of the Group IV metal. When the second temperature is in the range of 650° C. to 750° C., the diffusive duration will typically be in the range of 2 hours to 40 hours.
In a specific embodiment, the gaseous oxidising species is CO2, the first temperature is in the range of 600° C. to 750° C., the oxidising duration is in the range of 1 hour to 8 hours, the second temperature is in the range of 650° C. to 750° C., and the diffusive duration is in the range of 2 to 8 times the oxidising duration, e.g. in the range of 2 hours to 64 hours. In another embodiment, the gaseous oxidising species is CO2, the first temperature and the second temperature are both in the range of 650° C. to 700° C. with the second temperature being higher than the first temperature, the oxidising duration is in the range of 2 hours to 6 hours, and the diffusive duration is in the range of 3 to 6 times the oxidising duration, e.g. in the range of 6 hours to 36 hours.
In other embodiments, the gaseous oxidising species is N2O and/or O2, the first temperature is in the range of 600° C. to 650° C., the oxidising duration is in the range of 30 minutes to 2 hours, the second temperature is in the range of 650° C. to 700° C., and the diffusive duration is in the range of 4 to 20 times the oxidising duration, e.g. in the range of 2 hours to 40 hours.
In a specific embodiment, the oxidising atmosphere further comprises CO. For example, the gaseous oxidising species may be CO2 and the oxidising atmosphere may contain both CO and CO2. The presence of carbon in the oxidising atmosphere will dissolve carbon in the Group IV metal, and carbon, even at trace levels, is believed to provide a more stable integration of the oxide layer with the diffusion zone between the core of the Group IV metal and the oxide layer, so that an extremely stable non-stratified oxide layer is formed. When the gaseous oxidising species is CO2, without CO added to the oxidising atmosphere, a more stable non-stratified oxide layer is formed than when the oxidising is O2 or N2O. However, when O2 or N2O is the gaseous oxidising species and the oxidising atmosphere is supplemented with CO, carbon will also be dissolved in the Group IV metal to afford a more stable non-stratified oxide layer. Other carbon containing molecules are also contemplated to dissolve carbon in the Group IV metal although hydrogen containing molecules, e.g. alkanes, should be avoided to prevent embrittlement of the Group IV metal.
When the oxidising atmosphere contains CO2 and CO, CO2 and CO will take part in Reaction 1 and Reaction 2 identified below.
CO(g)+½O2(g)=CO2(g) Reaction 1
2CO(g)=CO2(g)+C Reaction 2
In general, CO is considered to be a carbon providing molecule without oxidising capability, whereas CO2 has an oxidising potential but limiting carbon activity. The partial pressure of O2 (pO2) and the activity of carbon (ac) existing from Reaction 1 and Reaction 2 can be determined from Equation 1 and Equation 2. Thus, the partial pressure of O2 is:
and the activity of carbon is:
where ΔG1=−282.200+86.7 T (J), and ΔG2=−170.550+174.3 T (J).
By using a mixture of CO2 and CO, the amount of carbon dissolved into the Group IV metal can be controlled, and it is therefore possible to tailor the oxidising atmosphere to eventually also tailor the diffusion zone of the component of the invention. Carbon will generally increase the microhardness of the diffusion zone compared to a diffusion zone comprising oxygen but no carbon. Furthermore, CO is believed to provide a thicker diffusion zone together with a thinner oxide layer. The combination of the thinner oxide layer and thicker diffusion zone is considered advantageous in the subsequent the step of diffusing oxygen from the non-stratified Group IV metal oxide into the Group IV metal, since the oxygen atoms in the Group IV metal oxide will diffuse more efficiently into the Group IV metal. Moreover, without being bound by theory the present inventors believe that carbon in the Group IV metal oxide will further stabilise the non-stratified oxide layer thereby yielding an improved process compared to using only CO2, O2 or N2O as the gaseous oxidising species. In a specific embodiment, the oxidising atmosphere therefore has a mixture of CO2 and CO with 40% to 90% CO2 compared to the total of CO2 and CO. In another embodiment, the oxidising atmosphere has a mixture of CO2 and CO with 40% to 60% CO2 compared to the total of CO2 and CO. Similar ratios are relevant for other gaseous oxidising species, e.g. O2 or N2O. For example, the oxidising atmosphere may have a mixture of O2 and CO with 40% to 60% O2 compared to the total of O2 and CO. The oxidising atmosphere may also have a mixture of N2O and CO with 40% to 60% N2O compared to the total of N2O and CO.
Treatment of the Group IV metal in the oxidising atmosphere will dissolve oxygen into the Group IV metal so that a diffusion zone is formed between the core of the Group IV metal and the non-stratified oxide layer. In the context of the invention, a “diffusion zone” is any zone, e.g. identified from the surface of the Group IV metal to a depth in the Group IV metal, where oxygen is dissolved in the Group IV metal. Interstitial oxygen will harden the Group IV metal, and the diffusion zone can therefore be identified by measuring the hardness in the cross-section of the Group IV metal. After the diffusion step, the oxygen atoms from the non-stratified oxide layer have diffused into the Group IV metal so that only the unavoidable nanometer thickness oxide layer is present on the Group IV metal. The concentration of the interstitial oxygen will be highest at the surface of the hardened Group IV metal to decrease at increasing depth. In general, the diffusion zone is considered to extend from the surface of the Group IV metal to a depth where the cross-sectional hardness is at 120% of the hardness of the core of the Group IV metal.
It is preferred that the concentration of interstitial oxygen near the surface of the Group IV metal is close to saturation. A surface hardness of 1000 HV0.025 is available for any Group IV metal even though the oxygen content near the surface is lower than the saturation level for oxygen. A surface hardness of 650 HV0.025 is considered sufficient to provide scratch resistance to the hardened Group IV metal. A thickness of the diffusion zone of about 5 μm will allow that a surface hardness of 1000 HV0.025 is obtained. Thus, in a preferred embodiment, the diffusion zone has a thickness of at least 5 μm. The thickness of the diffusion zone is not limited although when the thickness if above 50 μm, no effect is observed for the increased thickness. Thus, in an embodiment the diffusion zone has a thickness in the range of 5 μm to 50 μm, i.e. a hardness of 120% of the core hardness of the Group IV metal can be recorded at a depth of 50 μm from the surface. The cross-section and the corresponding hardness profile of a hardened Grade 4 titanium is shown in
Removal of the non-stratified oxide layer is easily detected visually, by analysis of the cross-section, or by GDOES analysis. Visual inspection of the surface of the component will show if the component has a metallic lustre of if an oxide layer is present on the surface. Exemplary components are shown in
Exemplary GDOES analyses are shown in
When carbon is present in the oxidising atmosphere, e.g. when the gaseous oxidising species is CO2, or when the oxidising atmosphere is supplemented with CO, carbon will be present in the non-stratified oxide layer. Likewise, when nitrogen is present, e.g. as N2 or N2O, nitrogen will be present in the non-stratified oxide layer. The carbon content and/or the nitrogen content is/are detectable using GDOES, as evident from
The local maximum in the carbon intensity is also relevant when the oxidising atmosphere contains CO, and in this case the higher carbon activity will provide an even harder diffusion zone and also harder surface. Thus, when the oxidising atmosphere has a mixture of CO2 and CO with 40% to 60% CO2 compared to the total of CO2 and CO, when the oxidising atmosphere has a mixture of O2 and CO with 40% to 60% O2 compared to the total of O2 and CO, or when the oxidising atmosphere has a mixture of N2O and CO with 40% to 60% N2O compared to the total of N2O and CO, a surface hardness of at least 800 HV0.025 is available for Grade 5 titanium, and a surface hardness of at least 800 HV0.025 is available for Grade 2 titanium.
In general, all variations and features for any aspect and embodiment of the invention may be combined freely. The features described above for the method are thus equally relevant for the component of the invention.
In the following the invention will be explained in greater detail with the aid of an example and with reference to the schematic drawings, in which
Reference to the figures serves to explain the invention and should not be construed as limiting the features to the specific embodiments as depicted.
The present invention relates to a method of oxygen hardening a Group IV metal and to a Group IV metal component having a surface hardness of at least 200 HV0.025 higher than the core hardness.
In the context of the invention “Group IV metal” is any metal selected from the titanium group of the periodic table of the elements or an alloy comprising at least 50% of metals from the titanium group. Thus, a “titanium alloy” is any alloy containing at least 50% (a/a) titanium, and likewise a “zirconium alloy” is any alloy containing at least 50% (a/a) zirconium. It is contemplated that for the method of the invention and for the component of the invention any alloy containing a sum of titanium and zirconium of at least 50% (a/a) is appropriate. Likewise, the alloy may also comprise hafnium, which is a member of Group IV of the periodic table of the elements so that any alloy having a sum of titanium, zirconium, and hafnium of at least 50% (a/a) is appropriate for the invention.
Alloys of relevance to the invention may contain any other appropriate element, and in the context of the invention an “alloying element” may refer to a metallic component or element in the alloy, or any constituent in the alloy. Titanium and zirconium alloys are well-known to the skilled person. Alloys of Group IV metals may also comprise metals from other groups of the periodic table of the elements, e.g. aluminium or niobium. An exemplary niobium containing alloy is Ti13Nb13Zr. Aluminium containing alloys are Ti6Al4V (Grade 5), which exists as an “extra low interstitial” (ELI) version, Ti6Al4V ELI that is commonly referred to as Grade 23.
Any grade of titanium containing at least about 99% (w/w) titanium is, in the context of the invention, considered to be “pure titanium”, e.g. Grade 1 titanium, Grade 2 or Grade 4 titanium; thus, the pure titanium may contain up to about 1% (w/w) trace elements, e.g. oxygen, carbon, nitrogen or other metals, such as iron. Pure titanium may also be referred to as “commercially pure” (CP). In particular, nitrogen and carbon contained in a Group IV metal in the context of the invention may represent unavoidable impurities. Elements present as “unavoidable impurities” are considered not to provide an effect for a workpiece treated according to the method of the invention or for the component of the invention. Likewise, any grade of zirconium containing at least about 99% (w/w) zirconium is, in the context of the invention, considered to be “pure zirconium”.
When a percentage is stated for a metal or an alloy the percentage is by weight of the weight of material, e.g. denoted % (w/w), unless otherwise noted. When a percentage is stated for an atmosphere the percentage is by volume, e.g. denoted % (v/v), unless otherwise noted. Likewise, unless otherwise noted a composition of a mixture of gasses may be on an atomic basis and may then be provided as a percentage or in ppm (parts per million).
In the context of the invention the hardness is generally the HV0.025 as measured according to the DIN EN ISO 6507 standard. If not otherwise mentioned the unit “HV” thus refers to this standard. The hardness may be recorded for a cross-section, e.g. of a treated Group IV metal, and it may be noted with respect to the depth of the measurement. The hardness measurement in the cross-section may also be referred to as “microhardness”, and the hardness measurement at the surface may also be referred to as “macrohardness”.
The microhardness measurement is generally independent of the testing conditions, since the measurement is performed at microscale in the cross-section. Microhardness measurements are typically performed at a load of 25 g, i.e. HV0.025, or 50 g, i.e. HV0.05. In contrast, the macrohardness may be performed from the surface with a much higher load, e.g. 0.50 kg, corresponding to HV0.5, so that the measurement represents an overall value of the hardness of the respective material and whatever surface layers it contains. Microhardness measurements at loads of 25 g or 50 g typically provide the same value, “HV”, but measurement at 25 g is preferred since the measurement requires less space in the cross-section.
When the hardness is recorded at a cross-section the measurement is considered to represent a homogeneous sample with respect to the direction of the pressure applied. In contrast, when the hardness is obtained from measurements at the surface the measurement may represent an average of several different values of hardness, i.e. at different depths. Thus, when the surface hardness is measured at a high load, e.g. 0.50 kg, the value can be considered to provide an “average” value for both the surface and also depths below the surface. It is therefore preferred that surface hardness is measured with a load of 25 g or 50 g. When the surface hardness is measured with a load of 25 g, a value of 650 HV0.025 is considered to show that the material is scratch resistant. As an effect of the fact that oxygen is dissolved from the surface the content of dissolved oxygen will decrease from the surface towards the core of the Group IV metal, and likewise, the hardness will be maximal at the surface.
Specimens of CP Grade 4 titanium were provided and treated in a Netzsch STA449 C (furnace) using CO2 or a Netzsch STA449 F3 (furnace) using N2O as the gaseous oxidising species at ambient pressure at different first temperatures and oxidising durations. Following the oxidising treatments, the cross-sections of the treated samples were analysed microscopically. Thus,
In
A sample of Grade 4 titanium was treated with N2O for 64 minutes at ambient pressure at 600° C. This oxidising step was followed by the diffusion step conducted in vacuum at about 10−6 mbar at 750° C. for 4 hours. The treatment provided the sample with an unaffected surface finish so that the sample regained its metallic lustre. The cross-section of the hardened sample was analysed microscopically, and the hardness profile measured. The results are shown in
Workpieces with diameters of 15 mm and thicknesses of 2 mm of CP titanium (Grade 2) and Ti6Al4V ELI were treated in two separate steps.
In the first step, the oxidising step, a sample was placed in a MTI OFT-1200 glass tube furnace. The furnace was evacuated and backfilled with CO2. A continuous gas flow of 200 ml/min was used. The workpiece was heated to 650° C. at a rate of 12 K/m in. The furnace was kept at 650° C. for 4 hours after which the furnace was allowed to cool down to room temperature unaided.
In the second step, the diffusion step, the cooled workpiece from the first step was placed in a tube furnace with an Edwards 85 T-station turbo vacuum pump. The vacuum pump was allowed to evacuate the chamber to <10−3 mbar before the furnace was turned on. The furnace heats at a rate of approx. 50 K/min (>250° C.). The furnace was kept at 680° C. for 16 hours after which the furnace was cooled down to room temperature at a rate of approx. 25 K/min. The end pressure in the furnace chamber was <10−4 mbar.
Photos of the components are shown in
The cross-sections of (a), (b) and (c) of
The samples of Example 3 were further analysed using Glow Discharge Optical Emission Spectroscopy (GDOES) analysis, and the results are shown in
The GDOES analyses the content of specified elements shown as an intensity (in the unit V) over time (in second). Thus, the intensity reflects the relative amount of the element and the time reflects the depth from the surface. By analysing the sample for a sufficient time to reflect the composition of layers relevant for the workpiece or component, the GDOES analysis appropriately provides a comparison of the compositions of the untreated workpiece, the intermediary workpiece having the non-stratified oxide layer and the diffusion zone between the non-stratified oxide layer and the material core, and the core of the Group IV metal.
Thus,
A workpiece of Ti6Al4V (Grade 5) was treated to provide a component of the invention. Specifically, the workpiece was created by 3D printing as a cylindrical workpiece with a diameter of 12 mm and a height of 15 mm, and the workpiece was subsequently treated in two separate steps.
In the first step, the sample was placed in a MTI OFT-1200 glass tube furnace, which was evacuated and backfilled with CO2. A continuous gas flow of 200 ml/min was used. The workpiece was heated to 650° C. at a rate of 12 K/min. The furnace was kept at 650° C. for 4 hours after which the furnace was allowed to cool down to room temperature unaided.
In the second step, the diffusion step, the cooled workpiece from the first step was placed in a tube furnace with an Edwards 85 T-station turbo vacuum pump. The vacuum pump was allowed to evacuate the chamber to <10−3 mbar before the furnace was turned on. The furnace heats at a rate of approx. 50 K/min (>250° C.). The furnace was kept at 680° C. for 16 hours after which the furnace was cooled down to room temperature at a rate of approx. 25 K/min. The end pressure in the furnace chamber was <10−4 mbar. A photo and the hardness profile of the component are illustrated in
Workpieces with a diameter of 15 mm and a thickness of 2 mm were treated in two separate steps in a variant where CO was included in the oxidising atmosphere. The sample were of CP titanium of Grade 4 and Ti6Al4V (Grade 5).
In the first step, a sample was placed in a MTI OFT-1200 glass tube furnace. The furnace was evacuated and backfilled with CO2/C0 at a 50/50 ratio using a continuous gas flow of 200 ml/min. The workpiece was heated to 650° C. at a rate of 12 K/min. The furnace was kept at 650° C. for 4 hours after which the furnace was allowed to cool down to room temperature unaided.
In the second step, the cooled workpiece from the first step was placed in a tube furnace with an Edwards 85 T-station turbo vacuum pump. The vacuum pump was allowed to evacuate the chamber to <10−3 mbar before the furnace was turned on. The furnace heats at a rate of approx. 50 K/min (>250° C.). The furnace was kept at 680° C. for 16 hours after which the furnace was cooled down to room temperature at a rate of approx. 25 K/m in. The end pressure in the furnace chamber was <10−4 mbar.
The provided component showed a similar surface to the one seen on the component oxidised only in CO2, and the components thus provided regained their metallic lustre after the diffusion step.
Samples of CP titanium of Grade 4 and Ti6Al4V (Grade 5) with a diameter of 15 mm and a thickness of 2 mm were treated in a variant where ambient air at ambient pressure was used as the oxidising atmosphere.
In the first step, the sample was placed in a Nabertherm LE4/11 R6 furnace, and the sample was then heated to 650° C. at a rate of 12 K/m in. The furnace was kept at 650° C. for 4 hours after which the furnace was allowed to cool down to room temperature unaided.
In the second step, the cooled sample from the first step was placed in a tube furnace with an Edwards 85 T-station turbo vacuum pump. The vacuum pump was allowed to evacuate the chamber to <10−3 mbar before the furnace was turned on. The furnace heats at a rate of approx. 50 K/m in (>250° C.). The furnace was kept at 680° C. for 16 hours after which the furnace was cooled down to room temperature at a rate of approx. 25 K/m in. The end pressure in the furnace chamber was <10−4 mbar.
The components included interstitial nitrogen, which was reflected as a higher surface hardness. The Grade 4 titanium component had a surface similar to the one seen on the component oxidised only in CO2, whereas the Grade 5 titanium component was less aesthetically pleasing.
Samples of zirconium (Zr702) and a niobium containing alloy (Ti13Nb13Zr) were treated using CO2 as gaseous oxidising species at 650° C. for 4 hours followed by the diffusion step in vacuum for 16 hours at 680° C. as described in Example 3. The Ti13Nb13Zr workpiece had a diameter of 10 mm and a thickness of 1 mm, whereas the Zr702 workpiece was a square with a side length of 15 mm and a thickness of 1.5 mm.
The treatment resulted in surface hardnesses of the components of about 860 HV0.025 and about 1218 HV0.025, respectively for the Ti13Nb13Zr and the Zr702, compared to surface hardnesses of the workpieces of 264 HV0.025 and 185 HV0.025, respectively, before treatment.
A workpiece with a diameter of 15 mm and a thickness of 2 mm was treated in the two steps outlined in Example 3 followed by an additional anodisation step. The workpiece was of CP titanium grade 4.
In the third step, the anodisation step, the component was cleaned in first distilled water, followed by ethanol and then turpentine. The component was lowered into a solution containing 15% phosphoric acid. A voltage of 70 V was applied for 5 to 10 seconds. After the diffusion step, the component regained its metallic lustre, but the anodisation provide a visible oxide layer typical of anodised titanium that has not been treated in the method of the invention.
Experiment were conducted to define the limits for formation of stratified titanium oxide layers vs. non-stratified titanium oxide layers when using N2O as the gaseous oxidising species. Specifically, specimens of CP Grade 2 titanium were provided and treated as done in Example 1.
Following the oxidising treatments, the cross-sections of the treated samples were analysed microscopically, and the results are plotted in
A CP Titanium 030 mm disc with a thickness of 15 mm was polished to a mirror like surface finish. Prior to treatment the CP titanium specimen was polished to a mirror polished surface finish, i.e. having an arithmetical mean deviation (Ra) roughness of <0.1 μm (thus being in accordance with the ISO 1302:2002 standard). The Ra value was measured using a Taylor-Hubson Surtronic S25 measuring over a length of 1.25 mm. The measurement was repeated 12 times on the surface of the specimen. The mean Ra value was measured to <0.1 μm, and the surface of the specimen was approved as mirror polished.
The specimen was placed in a Nabertherm 3-Zone furnace. The furnace was evacuated and backfilled using CO2 twice. The furnace was then heated to 650° C. for 4 hours using a continuous flow of CO2 at 500 ml/min. The furnace was allowed to cool down using furnace cooling. The specimen was, for a 2nd treatment, placed in a furnace capable of achieving a pressure <10−4 mbar. The Furnace was heated to 680° C. and held there for 16 hours. The furnace was cooled down using furnace cooling.
The Ra value of the surface on the specimen was measured using the same procedure as prior to the thermochemical treatment (described above). The specimen still displays a surface roughness with a Ra value of <0.1 μm. The surface roughness is shown in
| Number | Date | Country | Kind |
|---|---|---|---|
| 19193358.9 | Aug 2019 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2020/073556 | 8/21/2020 | WO |
