Patent Grant
8025367
The invention relates to MEMS devices and in particular MEMS devices that vaporize liquid to generate a vapor bubble during operation.
Various methods, systems and apparatus relating to the present invention are disclosed in the following US patents/patent applications filed by the applicant or assignee of the present invention:
The disclosures of these applications and patents are incorporated herein by reference.
Some micro-mechanical systems (MEMS) devices process, or use liquids to operate. In one class of these liquid-containing devices, resistive heaters are used to heat the liquid to the liquid's superheat limit, resulting in the formation of a rapidly expanding vapor bubble. The impulse provided by the bubble expansion can be used as a mechanism for moving liquid through the device. This is the case in thermal inkjet printheads where each nozzle has a heater that generates a bubble to eject a drop of ink onto the print media. In light of the widespread use of inkjet printers, the present invention will be described with particular reference to its use in this application. However, it will be appreciated that the invention is not limited to inkjet printheads and is equally suited to other devices in which vapor bubbles formed by resistive heaters are used to move liquid through the device (e.g. some ‘Lab-on-a-chip’ devices).
The resistive heaters in inkjet printheads operate in an extremely harsh environment. They must heat and cool in rapid succession to form bubbles in the ejectable liquid—usually a water soluble ink with a superheat limit of approximately 300° C. Under these conditions of cyclic stress, in the presence of hot ink, water vapor, dissolved oxygen and possibly other corrosive species, the heaters will increase in resistance and ultimately go open circuit via a combination of oxidation and fatigue, accelerated by mechanisms that corrode the heater or its protective oxide layers (chemical corrosion and cavitation corrosion).
To protect against the effects of oxidation, corrosion and cavitation on the heater material, inkjet manufacturers use stacked protective layers, typically made from Si3N4, SiC and Ta. In certain prior art devices, the protective layers are relatively thick. U.S. Pat. No. 6,786,575 to Anderson et al (assigned to Lexmark) for example, has 0.7 μm of protective layers for a ˜0.1 μm thick heater. To form a vapor bubble in the bubble forming liquid, the surface of the protective layers in contact with the bubble forming liquid must be heated to the superheat limit of the liquid (˜300° C. for water). This requires that the entire thickness of the protective layers be heated to (or in some cases above) the liquid superheat limit. Heating this additional volume decreases the efficiency of the device and significantly increases the level of residual heat present after firing. If this additional heat cannot be removed between successive firings of the nozzle, the ink in the nozzles will boil continuously, causing the nozzles to cease ejecting droplets in the intended manner.
The primary cooling mechanism of printheads on the market is currently thermal conduction, with existing printheads implementing a large heat sink to dissipate heat absorbed from the printhead chip. The ability of this heatsink to cool the liquid in the nozzles is limited by the thermal resistance between the nozzles and the heatsink and by the heat flux generated by the firing nozzles. As the extra energy required to heat the protective layers of a coated heater contributes to an increased heat flux, more severe constraints are imposed on the density of the nozzles on the printhead and the nozzle firing rate. This in turn has an impact on the print resolution, the printhead size, the print speed and the manufacturing costs.
Accordingly the present invention provides an inkjet printhead for ejecting drops of liquid on to a media substrate, the inkjet printhead comprising:
Titanium aluminium (TiAl) alloys exhibit superior strength, low creep and light weight; properties which have seen these alloys widely used in the aeronautical and automotive industries. However, the Applicant's work has revealed that TiAl is also well suited to use as a heater material in inkjet printheads. The alloy can provide surface oxide that is a uniform, thin and dense coating of predominantly Al2O3, which has very low oxygen diffusivity. Accordingly, the native (i.e. naturally forming) oxide layer passivates the heater to guard against oxidative failure while remaining thin enough not thermally insulate the heater from the ink. This preserves the low energy ejection of drops that is necessary for large (pagewidth), high density nozzle arrays, without compromising the operational life of the heater.
Further improvement in oxidation resistance can be obtained with additive element X, which has been found to enhance the diffusivity of aluminium, thereby encouraging the formation of Al2O3 whilst suppressing the formation of TiO2. TiO2 has much higher oxygen diffusivity than Al2O3, so suppressing its formation relative to Al2O3 provides improved oxidation resistance.
Optionally X is W, or X includes W which contributes between 1.7% and 4.5% by weight.
Optionally Ti contributes more than 48% by weight, Al contributes more than 48% by weight and X is 0% by weight.
Optionally the TiAl component of the heater has a gamma phase structure.
Optionally the heater has a microstructure with a grain size less than 100 nanometers.
Optionally the TiAlX alloy forms an Al2O3 surface oxide which directly contacts the liquid during use.
Optionally the TiAlX alloy is deposited as a layer less than 2 microns thick. Preferably the layer is less than 0.5 microns thick.
Optionally the heater further comprises a protective coating, the protective coating having a total thickness less than 0.5 microns. Optionally the protective coating is a single layer of material. Optionally the protective coating is at least partially formed from a silicon oxide, nitride or carbide.
In a second aspect the present invention provides a MEMS device for generating a bubble, the MEMS device comprising:
A grain size less than 100 nm (a “nanocrystalline” microstructure) is beneficial in that it provides good material strength yet has a high density of grain boundaries. Compared to a material with much larger crystals and a lower density of grain boundaries, the nanocrystalline structure provides higher diffusivity for the protective scale forming elements Cr and Al (more rapid formation of the scale) and a more even growth of the scale over the heater surface, so the protection is provided more rapidly and more effectively. The protective scales adhere better to the nanocrystalline structure, which results in reduced spalling. Further improvement in the mechanical stability and adherence of the scale is possible using additives of reactive metal from the group consisting of yttrium, lanthanum and other rare earth elements.
The primary advantage of an oxide scale that passivates the heater is it removes the need for additional protective coatings. This improves efficiency as there is no energy wasted in heating the coatings. As a result, the input energy required to form a bubble with a particular impulse is reduced, lowering the level of residual heat in the printhead. The majority of the remaining heat can be removed via the ejected drops, a mode of operation known as “self cooling”. The primary advantage of this mode of operation is that the design is not reliant on conductive cooling, so a heatsink is not required and the nozzle density and firing rate constraints imposed by conductive cooling are removed, allowing increased print resolution and speed and reduced printhead size and cost.
Optionally, the chamber has a nozzle opening such that the pressure pulse ejects a drop of the liquid through the nozzle opening.
Optionally the chamber has an inlet for fluid communication with a supply of the liquid such that liquid from the supply flows into the chamber to replace the drop of liquid ejected through the nozzle opening.
Optionally the heater is deposited by a super alloy deposited by a sputtering process.
Optionally the heater element is deposited as a layer of the superalloy less than 2 microns thick.
Optionally the superalloy has a Cr content between 2% by weight and 35% by weight.
Optionally the superalloy has a Al content of between 0.1% by weight and 8.0% by weight.
Optionally the superalloy has a Mo content of between 1% by weight and 17.0% by weight
Optionally the superalloy has a Nb and/or Ta content totalling between 0.25% by weight and 8.0% by weight.
Optionally the superalloy has a Ti content of between 0.1% by weight and 5.0% by weight.
Optionally the superalloy has up to 5% by weight of reactive metal from the group consisting of yttrium, lanthanum and other rare earth elements
Optionally the superalloy has a Fe content of up to 60% by weight.
Optionally the superalloy has a Ni content of between 25% by weight and 70% by weight.
Optionally the superalloy has a Co content of between 35% by weight and 65% by weight.
Optionally the superalloy is MCrAlX, where M is one or more of Ni, Co, Fe with M contributing at least 50% by weight, Cr contributing between 8% and 35% by weight, Al contributing more than zero but less than 8% by weight, and X contributing less than 25% by weight, with X consisting of zero or more other elements, preferably including but not limited to Mo, Re, Ru, Ti, Ta, V, W, Nb, Zr, B, C, Si, Y, Hf.
Optionally the superalloy comprises Ni, Fe, Cr and Al together with additives consisting of zero or more other elements, preferably including but not limited to Mo, Re, Ru, Ti, Ta, V, W, Nb, Zr, B, C, Si, Y, or Hf.
Optionally the superalloy is selected from:
INCONEL™ Alloy 600, Alloy 601, Alloy 617, Alloy 625, Alloy 625LCF, Alloy 690, Alloy 693, Alloy 718, Alloy 783, Alloy X-750, Alloy 725, Alloy 751, Alloy MA754, Alloy MA758, Alloy 925, or Alloy HX;
INCOLOY™ Alloy 330, Alloy 800, Alloy 800H, Alloy 800HT, Alloy MA956, Alloy A-286, or Alloy DS;
NIMONIC™ Alloy 75, Alloy 80A, or Alloy 90;
BRIGHTRAY® Alloy B, Alloy C, Alloy F, Alloy S, or Alloy 35; or,
FERRY® Alloy or Thermo-Span® Alloy
Preferred embodiments of the present invention will now be described, by way of example only with reference to the accompanying drawings in which:
In the description that follows, corresponding reference numerals, or corresponding prefixes of reference numerals (i.e. the parts of the reference numerals appearing before a point mark) which are used in different figures relate to corresponding parts. Where there are corresponding prefixes and differing suffixes to the reference numerals, these indicate different specific embodiments of corresponding parts.
Overview of the Invention and General Discussion of Operation
With reference to
The printhead also includes, with respect to each nozzle 3, side walls 6 on which the nozzle plate is supported, a chamber 7 defined by the walls and the nozzle plate 2, a multi-layer substrate 8 and an inlet passage 9 extending through the multi-layer substrate to the far side (not shown) of the substrate. A looped, elongate heater element 10 is suspended within the chamber 7, so that the element is in the form of a suspended beam. The printhead as shown is a microelectromechanical system (MEMS) structure, which is formed by a lithographic process which is described in more detail below.
When the printhead is in use, ink 11 from a reservoir (not shown) enters the chamber 7 via the inlet passage 9, so that the chamber fills to the level as shown in
Turning briefly to
When the element 10 is heated as described above, the bubble 12 forms along the length of the element, this bubble appearing, in the cross-sectional view of
The bubble 12, once generated, causes an increase in pressure within the chamber 7, which in turn causes the ejection of a drop 16 of the ink 11 through the nozzle 3. The rim 4 assists in directing the drop 16 as it is ejected, so as to minimize the chance of drop misdirection.
The reason that there is only one nozzle 3 and chamber 7 per inlet passage 9 is so that the pressure wave generated within the chamber, on heating of the element 10 and forming of a bubble 12, does not affect adjacent chambers and their corresponding nozzles. However, it is possible to feed ink to several chambers via a single inlet passage as long as pressure pulse diffusing structures are positioned between chambers. The embodiment shown in
The advantages of the heater element 10 being suspended rather than embedded in any solid material, are discussed below. However, there are also advantages to bonding the heater element to the internal surfaces of the chamber. These are discussed below with reference to
The increase in pressure within the chamber 7 not only pushes ink 11 out through the nozzle 3, but also pushes some ink back through the inlet passage 9. However, the inlet passage 9 is approximately 200 to 300 microns in length, and is only about 16 microns in diameter. Hence there is a substantial inertia and viscous drag limiting back flow. As a result, the predominant effect of the pressure rise in the chamber 7 is to force ink out through the nozzle 3 as an ejected drop 16, rather than back through the inlet passage 9.
Turning now to
The collapsing of the bubble 12 towards the point of collapse 17 causes some ink 11 to be drawn from within the nozzle 3 (from the sides 18 of the drop), and some to be drawn from the inlet passage 9, towards the point of collapse. Most of the ink 11 drawn in this manner is drawn from the nozzle 3, forming an annular neck 19 at the base of the drop 16 prior to its breaking off.
The drop 16 requires a certain amount of momentum to overcome surface tension forces, in order to break off. As ink 11 is drawn from the nozzle 3 by the collapse of the bubble 12, the diameter of the neck 19 reduces thereby reducing the amount of total surface tension holding the drop, so that the momentum of the drop as it is ejected out of the nozzle is sufficient to allow the drop to break off.
When the drop 16 breaks off, cavitation forces are caused as reflected by the arrows 20, as the bubble 12 collapses to the point of collapse 17. It will be noted that there are no solid surfaces in the vicinity of the point of collapse 17 on which the cavitation can have an effect.
Manufacturing Process for Suspended Heater Element Embodiments.
Relevant parts of the manufacturing process of a printhead according to embodiments of the invention are now described with reference to
Referring to
Guard rings 26 are formed in the metallization of the interconnect layers 23 to prevent ink 11 from diffusing from the region, designated 27, where the nozzle of the unit cell 1 will be formed, through the substrate portion 21 to the region containing the wiring 25, and corroding the CMOS circuitry disposed in the region designated 22.
The first stage after the completion of the CMOS fabrication process consists of etching a portion of the passivation layer 24 to form the passivation recesses 29.
If, instead, the hole 32 were to be etched all the way to the interconnect layers 23, then to avoid the hole 32 being etched so as to destroy the transistors in the region 22, the hole 32 would have to be etched a greater distance away from that region so as to leave a suitable margin (indicated by the arrow 34) for etching inaccuracies. But the etching of the hole 31 from the top of the substrate portion 21, and the resultant shortened depth of the hole 32, means that a lesser margin 34 need be left, and that a substantially higher packing density of nozzles can thus be achieved.
Then, the sacrificial resist of each of the resist layers 35, 39, 42 and 48, is removed using oxygen plasma, to form the structure shown in
Bonded Heater Element Embodiments
In other embodiments, the heater elements are bonded to the internal walls of the chamber. Bonding the heater to solid surfaces within the chamber allows the etching and deposition fabrication process to be simplified. However, heat conduction to the silicon substrate can reduce the efficiency of the nozzle so that it is no longer ‘self cooling’. Therefore, in embodiments where the heater is bonded to solid surfaces within the chamber, it is necessary to take steps to thermally isolate the heater from the substrate.
One way of improving the thermal isolation between the heater and the substrate is to find a material with better thermal barrier properties than silicon dioxide, which is the traditionally used thermal barrier layer, described in U.S. Pat. No. 4,513,298. The Applicant has shown that the relevant parameter to consider when selecting the barrier layer, is the thermal product; (pCk)1/2. The energy lost into a solid underlayer in contact with the heater is proportional to the thermal product of the underlayer, a relationship which may be derived by considering the length scale for thermal diffusion and the thermal energy absorbed over that length scale. Given that proportionality, it can be seen that a thermal barrier layer with reduced density and thermal conductivity will absorb less energy from the heater. This aspect of the invention focuses on the use of materials with reduced density and thermal conductivity as thermal barrier layers inserted underneath the heater layer, replacing the traditional silicon dioxide layer. In particular, this aspect of the invention focuses on the use of low-k dielectrics as thermal barriers
Low-k dielectrics have recently been used as the inter-metal dielectric of copper damascene integrated circuit technology. When used as an inter-metal dielectric, the reduced density and in some cases porosity of the low-k dielectrics help reduce the dielectric constant of the inter-metal dielectric, the capacitance between metal lines and the RC delay of the integrated circuit. In the copper damascene application, an undesirable consequence of the reduced dielectric density is poor thermal conductivity, which limits heat flow from the chip. In the thermal barrier application, low thermal conductivity is ideal, as it limits the energy absorbed from the heater.
Two examples of low-k dielectrics suitable for application as thermal barriers are Applied Material's Black Diamond™ and Novellus' Coral™, both of which are CVD deposited SiOCH films. These films have lower density than SiO2 (˜1340 kgm−3 vs ˜2200 kgm−3) and lower thermal conductivity (˜0.4 Wm−1 K−1 vs ˜1.46 Wm−1 K−1). The thermal products for these materials are thus around 600 Jm−2K−1s−1/2, compared to 1495 Jm−2K−1s−1/2 for SiO2 i.e. a 60% reduction in thermal product. To calculate the benefit that may be derived by replacing SiO2 underlayers with these materials, models using equation 3 in the Detailed Description can be used to show that ˜35% of the energy required to nucleate a bubble is lost by thermal diffusion into the underlayer when SiO2 underlayers are used. The benefit of the replacement is therefore 60% of 35% i.e. a 21% reduction in nucleation energy. This benefit has been confirmed by the Applicant by comparing the energy required to nucleate a bubble on
The latter required 20% less energy for the onset of bubble nucleation, as determined by viewing the bubble formation stroboscopically in an open pool boiling configuration, using water as a test fluid. The open pool boiling was run for over 1 billion actuations, without any shift in nucleation energy or degradation of the bubble, indicating the underlayer is thermally stable up to the superheat limit of the water i.e. ˜300° C. Indeed, such layers can be thermally stable up to 550° C., as described in work related to the use of these films as Cu diffusion barriers (see “Physical and Barrier Properties of Amorphous Silicon-Oxycarbide Deposited by PECVD from Octamethylcycltetrasiloxane”, Journal of The Electrochemical Society, 151 (2004) by Chiu-Chih Chiang et. al.).
Further reduction in thermal conductivity, thermal product and the energy required to nucleate a bubble may be provided by introducing porosity into the dielectric, as has been done by Trikon Technologies, Inc. with their ORION™ 2.2 porous SiOCH film, which has a density of ˜1040 kgm−3 and thermal conductivity of ˜0.16 Wm−1K−1 (see IST 2000 30043, “Final report on thermal modeling”, from the IST project “Ultra Low K Dielectrics For Damascene Copper Interconnect Schemes”). With a thermal product of ˜334 Jm−2K−1s−1/2, this material would absorb 78% less energy than a SiO2 underlayer, resulting in a 78*35%=27% reduction in the energy required to nucleate a bubble. It is possible however that the introduction of porosity may compromise the moisture resistance of the material, which would compromise the thermal properties, since water has a thermal product of 1579 Jm−2K−1s−1/2, close to that of SiO2. A moisture barrier could be introduced between the heater and the thermal barrier, but the heat absorption in this layer would likely degrade overall efficiency: in the preferred embodiment the thermal barrier is directly in contact with the underside of the heater. If it is not in direct contact, the thermal barrier layer is preferably no more than 1 μm away from the heater layer, as it will have little effect otherwise (the length scale for heat diffusion in the ˜1 μs time scale of the heating pulse in e.g. SiO2 is ˜1 μm).
An alternative for further lowering thermal conductivity without using porosity is to use the spin-on dielectrics, such as Dow Corning's SiLK™, which has a thermal conductivity of 0.18 Wm−1K−1. The spin-on films can also be made porous, but as with the CVD films, that may compromise moisture resistance. SiLK has thermal stability up to 450° C. One point of concern regarding the spin-on dielectrics is that they generally have large coefficients of thermal expansion (CTEs). Indeed, it seems that reducing k generally increases the CTE. This is implied in “A Study of Current Multilevel Interconnect Technologies for 90 nm Nodes and Beyond”, by Takayuki Ohba, Fujitsu magazine, Volume 38-1, paper 3. SiLK, for example, has a CTE of ˜70 ppm·K−1. This is likely to be much larger than the CTE of the overlying heater material, so large stresses and delamination are likely to result from heating to the ˜300° C. superheat limit of water based ink. SiOCH films, on the other hand, have a reasonably low CTE of ˜10 ppm·K−1, which in the Applicant's devices, matches the CTE of the TiAlN heater material: no delamination of the heater was observed in the Applicant's open pool testing after 1 billion bubble nucleations. Since the heater materials used in the inkjet application are likely to have CTEs around ˜10 ppm·K−1, the CVD deposited films are preferred over the spin-on films.
One final point of interest relating to this application relates to the lateral definition of the thermal barrier. In U.S. Pat. No. 5,861,902 the thermal barrier layer is modified after deposition so that a region of low thermal diffusivity exists immediately underneath the heater, while further out a region of high thermal diffusivity exists. The arrangement is designed to resolve two conflicting requirements:
Such an arrangement is unnecessary in the Applicant's nozzles, which are designed to be self cooling, in the sense that the only heat removal required by the chip is the heat removed by ejected droplets. Formally, ‘self cooled’ or ‘self cooling’ nozzles can be defined to be nozzles in which the energy required to eject a drop of the ejectable liquid is less than the maximum amount of thermal energy that can be removed by the drop, being the energy required to heat a volume of the ejectable fluid equivalent to the drop volume from the temperature at which the fluid enters the printhead to the heterogeneous boiling point of the ejectable fluid. In this case, the steady state temperature of the printhead chip will be less than the heterogenous boiling point of the ejectable fluid, regardless of nozzle density, firing rates or the presence or otherwise of a conductive heatsink. If a nozzle is self cooling, the heat is removed from the front face of the printhead via the ejected droplets, and does not need to be transported to the rear face of the chip. Thus the thermal barrier layer does not need to be patterned to confine it to the region underneath the heaters. This simplifies the processing of the device. In fact, a CVD SiOCH may simply be inserted between the CMOS top layer passivation and the heater layer. This is now discussed below with reference to
Roof Bonded and Floor Bonded Heater Elements
Referring firstly to
Bonded Heater Element Manufacturing Process
The unit cells shown in
The passivation layer may be a single silicon dioxide layer is deposited over the interconnect layers 23. Optionally, the passivation layer 24 can be a silicon nitride layer between two silicon dioxide layers (referred to as an “ONO” stack). The passivation layer 24 is planarised such that its thickness on the M4 layers 50 is preferably 0.5 microns. The passivation layer separates the CMOS layers from the MEMS structures and is also used as a hard mask for the ink inlet etch described below.
After this, a layer photoresist 42 is again spun onto the wafer 8 as shown in
Once the photoresist layer 42 is removed, another layer of photoresist 35 is spun onto the wafer as shown in
With the photoresist 35 defining the chamber roof and support walls, a layer of roof material, such as silicon nitride, is deposited onto the sacrificial scaffolding. In the embodiment shown in
The wafer 8 is then turned over so that the ‘backside’ 70 (see
In use, ink is fed from the backside 70 into the channel 32 and into the front side inlet 31. Gas bubbles are prone to form in the ink supply lines to the printhead. This is due to outgassing where dissolved gasses come out of solution and collect as bubbles. If the bubbles are fed into the chambers 7 with the ink, they can prevent ink ejection from the nozzles. The compressible bubbles absorb the pressure generated by the nucleating bubbles on the heater elements 10 and so the pressure pulse is insufficient to eject ink from the aperture 3. As the ink primes the chambers 7, any entrained bubbles will tend to follow the columnar features on either side of the ink inlet 31 and be pushed toward the bubble vent 66. Bubble vent 66 is sized such that the surface tension of the ink will prevent ink leakage, but trapped gas bubbles can vent. Each heater element 10 is enclosed on three sides by chamber walls and by additional columnar features on the fourth side. These columnar features diffuse the radiating pressure pulse to lower cross-talk between chambers 7.
Superalloy Heaters
Superalloys are a class of materials developed for use at elevated temperatures. They are usually based on elements from Group VIIA of the Periodic Table and predominantly used in applications requiring high temperature material stability such as jet engines, power station turbines and the like. Their suitability in the thermal inkjet realm has until now gone unrecognized. Superalloys can offer high temperature strength, corrosion and oxidation resistance far exceeding that of conventional thin film heaters (such as tantalum aluminium, tantalum nitride or hafnium diboride) used in known thermal inkjet printheads. The primary advantage of superalloys is that they can have sufficient strength, oxidation and corrosion resistance to allow heater operation without protective coatings, so that the energy wasted in heating the coatings is removed from the design—as discussed in the parent specification U.S. Ser. No. 11/097,308.
Testing has indicated that superalloys can in some cases have far superior lifetimes compared to conventional thin film materials when tested without protective layers.
The applicant's prior work indicates that oxidation resistance is strongly correlated with heater lifetime. Adding Al to TiN to produce TiAlN greatly increased the heater's oxidation resistance (measured by Auger depth profiling of oxygen content after furnace treatment) and also greatly increased heater lifetime. The Al diffused to the surface of the heater and formed a thin oxide scale with a very low diffusivity for further penetration of oxygen. It is this oxide scale which passivates the heater, protecting it from further attack by an oxidative or corrosive environment, permitting operation without protective layers. Sputtered Inconel 718 also exhibits this form of protection and also contains Al, but has two other advantageous properties that further enhance oxidation resistance; the presence of Cr, and a nanocrystalline structure.
Chromium behaves in a similar fashion to aluminium as an additive, in that it provides self passivating properties by forming a protective scale of chromium oxide. The combination of Cr and Al in a material is thought to be better than either in isolation because the alumina scale grows more slowly than the chromia scale, but ultimately provides better protection The Cr addition is beneficial because the chromia scale provides short term protection while the alumina scale is growing, allowing the concentration of Al in the material required for short term protection to be reduced. Reducing the Al concentration is beneficial because high Al concentrations intended for enhanced oxidation protection can jeopardize the phase stability of the material.
X-ray diffraction and electron microscope studies of the sputtered Inconel 718 showed a crystalline microstructure, with a grain size less than 100 nm (a “nanocrystalline” microstructure). The nanocrystalline microstructure of Inconel 718 is beneficial in that it provides good material strength yet has a high density of grain boundaries. Compared to a material with much larger crystals and a lower density of grain boundaries, the nanocrystalline structure provides higher diffusivity for the protective scale forming elements Cr and Al (more rapid formation of the scale) and a more even growth of the scale over the heater surface, so the protection is provided more rapidly and more effectively. The protective scales adhere better to the nanocrystalline structure, which results in reduced spalling. Further improvement in the mechanical stability and adherence of the scale is possible using additives of reactive metal from the group consisting of yttrium, lanthanum and other rare earth elements.
It should be noted that superalloys are typically cast or wrought and this does not yield a nanocrystalline microstructure: the benefits provided by the nanocrystalline structure are specific to the sputtering technique used in the MEMS heater fabrication of this application. It should also be noted that the benefits of superalloys as heater materials are not solely related to oxidation resistance: their microstructure is carefully engineered with additives to encourage the formation of phases that impart high temperature strength and fatigue resistance. Potential additions comprise the addition of aluminium, titanium, niobium, tantalum, hafnium or vandium to form the gamma prime phase of Ni based superalloys; the addition of iron, cobalt, chrome, tungsten, molybdenum, rhenium or ruthenium to form the gamma phase or the addition of C, Cr, Mo, W, Nb, Ta, Ti to form carbides at the grain boundaries. Zr and B may also be added to strengthen grain boundaries. Controlling these additives, and the material fabrication process, can also act to suppress undesirable age-induced Topologically Close Packed (TCP) phases, such as sigma, eta, mu phases which can cause embrittlement, reducing the mechanical stability and ductility of the material. Such phases are avoided as they may also act to consume elements that would otherwise be available for the favoured gamma and gamma prime phase formation. Thus, while the presence of Cr and Al to provide oxidation protection is preferred for the heater materials, superalloys in general can be considered a superior class of materials from which selection of heater material candidates may be made, since considerably more effort has been put into designing them for high temperature strength, oxidation and corrosion resistance than has been put into improving the conventional thin film heater materials used in MEMS.
The Applicant's results indicate that superalloys:
Superalloy's having the generic formula MCrAlX where:
In particular, superalloys with Ni, Fe, Cr and Al together with additives comprising zero or more of Mo, Re, Ru, Ti, Ta, V, W, Nb, Zr, B, C, Si, Y, or Hf, show superior results.
Using these criteria, suitable superalloy material for thermal inkjet printhead heaters may be selected from:
INCONEL™ Alloy 600, Alloy 601, Alloy 617, Alloy 625, Alloy 625LCF, Alloy 690, Alloy 693, Alloy 718, Alloy X-750, Alloy 725, Alloy 751, Alloy MA754, Alloy MA758, Alloy 783, Alloy 925, or Alloy HX;
INCOLOY™ Alloy 330, Alloy 800, Alloy 800H, Alloy 800HT, Alloy MA956, Alloy A-286, or Alloy DS;
NIMONIC™ Alloy 75, Alloy 80A, or Alloy 90;
BRIGHTRAY® Alloy B, Alloy C, Alloy F, Alloy S, or Alloy 35; or,
FERRY® Alloy or Thermo-Span® Alloy
Brightray, Ferry and Nimonic are the registered trademarks of Special Metals Wiggin Ltd Holmer Road HEREFORD HR4 9FL UNITED KINGDOM.
Thermo-Span is a registered trademark of CRS holdings Inc., a subsidiary of Carpenter Technology Corporation.
Titanium Aluminium Alloy Heaters
Titanium aluminium (TiAl) alloys exhibit superior strength, low creep and light weight; properties which have seen these alloys widely used in the aeronautical and automotive industries. It's resistance to oxidation at extremely high temperatures makes it a suitable refractory coating for furnaces, kilns and the like (see “Oxidation Resistance of Refractory γ-TiAlW Coatings”, L. Kaczmarck et al. Surface & Coatings Technology 201 (2007) 6167-6170).
The Applicant's work has revealed that TiAl is also well suited to use as heater material in inkjet printheads. The alloy can provide surface oxide that is a uniform, thin and dense coating of predominantly Al2O3 and very little TiO2. Al2O3 has low oxygen diffusivity while TiO2 has a much higher diffusivity. Accordingly, the native (i.e. naturally forming) oxide layer passivates the heater to guard against oxidative failure while remaining thin enough not thermally insulate the heater from the ink. This preserves the low energy ejection of drops that is necessary for large (pagewidth), high density nozzle arrays, without compromising the operational life of the heater. Tests using a 0.2 micron thick TiAl heater have achieved 180 millions ejections with good print quality.
Other elements can be added to the alloy to further suppress the formation of TiO2 and/or increase Al diffusivity to the heater surface (and therefore preferential formation of Al2O3). Ag, Cr, Mo, Nb, Si, Ta and W, individually or in combination, enhance Al2O3 and suppress the less protective TiO2. The additives should not exceed 5% by weight of the TiAl alloy in total. Of these, W provides the alloy with an oxide scale having the best oxidative resistance. Adding W in the range 1.7 wt. % to 4.5 wt. % provides superior results.
Another advantage of adding W is that it is already used during integrated circuit fabrication. The vias through the inter-layer dielectric material (between the metal layers) of the CMOS are typically W. Using W in the ejection heaters is less likely to cause detrimental contamination of other components in the integrated circuit or MEMS.
The microstructure of the TiAl is another important aspect. Gamma phase TiAl provides a lattice substrate that is complementary to alpha phase Al2O3 (known as corundum). Hence the adherence of the oxide layer to the underlying metal is strong. Also the grain size of the microstructure should be nanocrystalline range. The nanocrystalline structure gives a high density of grain boundaries which promotes diffusivity of Al to the surface. This further promotes a dense and mechanically stable oxide scale. It will be appreciated that a nanocrystalline structure is easily achieved by magnetron sputtering the heater material such that grain sizes are below 100 nano-meters.
The thin, dense Al2O3 layer gives the heater an operational life comparable to that of existing inkjet printheads. While the oxygen diffusivity through the oxide is low, some oxygen will continue to reach. However, the operational life can be extended, albeit with some compromise on ejection efficiency, by adding a thin protective coating on the TiAl heater. A very thin protective coating (less than 0.5 microns thick) in conjunction with the protection of the native oxide scale will greatly enhance the operation life without substantially reducing the energy efficiency of droplet ejection. The protective coating can be a single layer or a laminate of different materials. Silicon oxides, silicon nitrides and silicon carbides form suitable protective coatings for inkjet heater elements.
The present invention has been described herein by way of example only. Ordinary workers in this field will readily recognize many variations and modifications which do not depart from the spirit and scope of the broad inventive concept.
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|---|---|---|---|
| 6425964 | Deevi et al. | Jul 2002 | B1 |
| 20050280672 | Silverbrook et al. | Dec 2005 | A1 |
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| 1657061 | May 2006 | EP |
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| WO 0064805 | Nov 2000 | WO |
| Number | Date | Country | |
|---|---|---|---|
| 20100097429 A1 | Apr 2010 | US |
