Patent Description:
The quest for higher electromechanical coupling coefficient in piezoelectric thin films is driven by the commercial need of advances in microelectromechanical devices (MEMS) for a variety of applications; such as wide-band filters operating at high radio frequency (above <NUM>) for wireless applications, miniaturized loudspeakers and microphones, just to name a few. Among the various strategies proposed, the partial substitution of Al by Sc in a Wurtzite AlN lattice outstands, due to the high figure of merit achievable and the possibility of integration into CMOS structures and the compatibility with front-end semiconductor equipment.

AlN has been the dominant material for piezoelectric thin film applications for many years. The major drawback of this material, i.e. the lower electromechanical coupling coefficient with respect to other class of materials, can be overcame with the substitution of Sc in the Wurtzite lattice since the longitudinal piezoelectric activity increases by up to four times for Sc/(Sc+Al) ratios up to <NUM>%[Akyama et al, Adv. <NUM>, <NUM>]. It has been proven moreover, both theoretically [<NPL>] and experimentally [<NPL>;], that a structural instability at the heart of piezoelectric anomaly in this class of materials can be introduced successfully with various substitutions of metallic elements "Me" (such as Y, or (Mg<NUM>,Zr<NUM>)) in the Wurtzite structure of nitrides of group III elements "A" (such as AlN, GaN and InN). A volume production solution for the deposition of A<NUM>-xMexN Wurtzite films (such as Al(<NUM>-x)ScxN, Al(<NUM>-x)(Mg, Zr)xN or In<NUM>-xYxN) poses however new challenges. Excellent homogeneity of film stress, crystallinity and surface roughness is required across large surface substrates due to the enhanced dependency of the coupling coefficient on the film stress. However, with increasing Sc content the growth of the required Wurtzite structure with c-axis orientation is disturbed by the appearance of elevated cone like crystallites. Several authors [Fichtner et al. ] [<NPL>] have demonstrated that this case of abnormal grain growth is determined by a surface an anisotropy in the capturing cross section for different planes of the Wurtzite structure for an off-normal deposition flux. These unwanted grains are still in the Wurtzite phase, but they are non c-axis oriented. Due to the competitive growth mechanism, since the ad-atom mobility oh these surfaces is lower, the growth of these grains is enhanced, and the result are grains of abnormal size which do not contribute in a relevant way to the piezoelectric activity of the film. This surface instability increases with the amount of Sc in the film. As a consequence the volume fraction of unwanted grains increases substantially with the Sc substitution. The likelihood of the appearance of these unwanted crystallites depends moreover strongly on the substrate/ A1<NUM>-xScxN interface. The nucleation of the Wurtzite phase occurs indeed at a very high rate: higher surface roughness results therefore into a higher probability of nucleation of grain with c-axis pointing in a direction not perpendicular to the substrates, and with significant deviation from the incoming ad-atom flux direction. A high number of crystallites are typically observable for A1<NUM>-xScxN grown on molybdenum when the Sc concentration is higher than 15at% whereas platinum is less affected by this issue due to higher surface smoothness for a given film thickness. The choice and the microstructure of the substrate surface is anyhow strongly limited by device specifications. Therefore, a robust process solution in the deposition of the A1<NUM>-xScxN layer, which reduces the chances of off-axis grain formation is highly advantageous.

Due to the limited surface instability of pure AlN, the use of a thin seed layer without Scandium has turned out to be efficient to ensure the growth of the desired A1<NUM>-xScxN quality on various substrate types and materials. As an example, the initial growth of <NUM> AlN on a molybdenum electrode allows the deposition of A1<NUM>Sc<NUM>N films with purely c-axis oriented Wurtzite structure. The positive effect of the A1N seed layer on other substrate surfaces including pure silicon and Si0<NUM> has been demonstrated as well. However, with growing Sc concentrations e.g. to 30at% the mismatch between the structure of the seed and the A1<NUM>-xScxN layer tends to promote re-nucleation and the pure AlN seed layer strategy comes to its limits: the growth of undesirable crystallites cannot be suppressed efficiently enough. It is therefore a gist of the present invention to provide an improved seeding process which ensures the growth of an A<NUM>-xMexN layer, e.g. as mentioned AlScN-layers and should show no or negligible number of crystallites compared to other known layers of comparable high "B" content. It is a further gist of the invention to provide a method to produce such layers and provide a processing system to perform the method.

In <CIT> a piezoelectric thin-film resonator including a piezoelectric thin film which includes aluminum nitride containing Sc is disclosed, whereat the concentration of Sc is non-uniform in a thickness direction of the piezoelectric thin film.

<CIT> discloses a gallium nitride-based compound semiconductor light-emitting element, in which the concentration of Mg which is a p-type dopant in a p-GaN layer is adjusted in a range from <NUM>. 0x10<NUM> cm-<NUM> to <NUM>. 0x10<NUM> cm-<NUM>.

<CIT> discloses a process to deposit an additive AlN film containing at least one additive element selected from Sc, Y, Ti, Cr, Mg and Hf, by pulsed DC reactive sputtering, wherein a first layer with an electrical bias power applied to the film support and a second layer of the same composition with no or a lower bias power applied are deposited consecutively in a process chamber.

In <CIT> a process of depositing an epitaxial Group III nitride semiconductor film with N-face polarity on a conditioned substrate surface is disclosed, wherein surface conditioning and deposition process take place in different stations of a multi-chamber process system.

In <CIT> a method of making a piezoelectric device is disclosed where different layers are deposited in different chambers of a multi-chamber process system.

A<NUM>-xMexN layers refer to any A<NUM>-xMexN non-centrosymmetric layers constituted by any of the group-III element "A" (like boron, aluminum, gallium, indium and thallium), and comprising one or more metallic elements "Me" from the transition metal groups <NUM> to 6b, like Y, Zr, and Mg from the 2a group, or especially cubically crystallizing species of that groups like Sc, Nb, Mo, or from the lanthanides, like La, Pr, Nd, Sm Eu, Gd, Tb, Dy, Ho, Er, Tm, Lu or again especially cubically crystallizing species of that group like Ce and Yb. The atomic percentage of elements A and the element or mixture of elements Me may vary as long no explicit numbers are referred to, which means that AMeN or AlScN refers to any Me/(A+Me) or Sc/(Al+Sc) ratio, also referred to as Me or Sc(Scandium) ratio, and N may be in a stoichiometric, in a sub-stoichiometric, or in a hyperstoichiometric relation to the metallic components of the compound.

A Substrate may be any base material including also substrates precoated with different functional layer structures in the following referred to as precoating which can be applied in a different or the same coating system. Such precoatings may comprise as a mere example acoustic mirrors, where e.g. a silicon substrate comprises a layer stack from, e.g. Siox and W layers, or etch-stop layers such as SiOx, SiNx, SiNxOy, AlNx.

Surprisingly it has been found that AMeN coatings comprising, when starting from the substrate side, a rising concentration gradient of Me from a low or even zero Me concentration towards a high Me/(A+Me)-ratio can help efficiently to inhibit the appearance of unwanted elevated cone like crystallites, in the following also called spikes.

In an embodiment of the invention the substrate has a surface coated with a piezoelectric coating as defined by claim <NUM>.

In a further embodiment of the invention Me can be at least one of Sc, Mg, Hf, Nb, Mo, Ce, Y and Yb, whereby Sc is preferred.

The coating may further comprise a seed-layer ending at the start of said steadily rising of the transition layer, wherein said ratio is constant along a further thickness extent δ2 of said coating.

In a further embodiment the coating may comprise a top-layer starting at the end of said steadily rising of the transition layer, wherein said ratio is constant along a further thickness extent δ4 of said coating.

The transition layer may start or end at one of the limiting surfaces of said coating, e.g. it may start directly on the surface of the substrate, directly on the surface of an adhesion layer and/or end without a top-layer of constant Me/Al ratio. Therefor the transition layer can also be the only layer of the system and <MAT>.

In a further embodiment said steadily rising of the transition layer can start with said ratio being zero.

The Me concentration of said steadily rising can be at least approximately linear, e.g. like a ramp.

In addition the coating may further comprise an adhesion layer deposited directly on the substrate surface, which may consists of at least one of the following materials: Si, Mo, W, Pt, Ru, Ti.

The seed layer or, if no seed layer is provided, the transition layer may be deposited directly on the substrate S surface or, if provided, on the surface of the adhesion layer.

At least a surface of the substrate may consist of Si, SiOx or GaAs. The surface may be the surface of a wafer or a diced and embedded wafer.

The ratio at the end of said steadily rising of the transition layer can be higher <NUM>% Me, preferably equal or higher <NUM>% Me, e.g. in the range of <NUM> to <NUM> %, or even <NUM> to <NUM>%.

According to the invention, the surface of the transition layer has and the top-layer, as far as provided, can have a uniform surface quality of less than <NUM>, especially less than <NUM>, or even less than <NUM> spikes in any <NUM> x <NUM> surface area. Especially the following layer combinations on substrate S can be realized, the order of the list refers to the potential of improvement:.

Best practice examples and applicable thickness ranges can be found with the description of figures and in table <NUM>.

The invention is also directed to a method of depositing an inventive A<NUM>-xMexN coating as defined by claim <NUM>.

In one embodiment of the invention co-sputtering can be performed within a deposition area where the sputter cone of the first target (A target) and the sputter cone of the second target (Me target or AMe target) overlap. The overlapping deposition area may comprise at least <NUM>% to <NUM>%, or <NUM>% to <NUM>% of the substrate surface to be coated.

Sputtering can be also performed with two first targets and two second targets with cones respectively overlapping in the substrate plane. Therefore, first and second targets can be arranged alternatingly on a circle concentric to axis Z.

Any method using as mentioned overlapping sputter cones, e.g. of the first and second targets, may profit from easy alloying or mixing of different materials sputtered from different targets, which are mixed in the overlapping cones just as in the respective substrate surface area to be coated. To provide a big overlapping surface area in the target plane, targets will be usually angled in an angle α from a plane in parallel to a substrate plane toward the middle axis Z of a central substrate support. The angle α may be chosen from <NUM>° to <NUM>°, e.g. about <NUM>°± <NUM>°, see also example below.

In a further embodiment of the invention co-sputtering is performed by rotating at least one substrate in a distance D from and round a central axis Z' alternatingly through sputter cones (C1, C2) of at least one first target and at least one second target, whereby a higher sputter rate of the first or the second target and the rotation of the substrates is controlled in mutual dependence to deposit only one or a few atomic material layers per pass of the sputter cone of the target with the higher sputter rate, whereas the per pas contribution of the target with the lower sputter rate will be even lower, e.g. some atoms, one or some fewer atomic layers.

Further examples and process parameters how to realize the invention in practice can be found with the description of figures and in table <NUM>.

The invention is also directed to an AMeN multi-chamber process system (MCS) as defined by claim <NUM>.

In an embodiment of the process system the <NUM>nd target is made from one of Sc or Sc and Al, and the AMe-target from the sputter chamber is made from an AlSc-alloy or an AlSc-mixture having a Scandium ratio between <NUM> and <NUM> at% or between <NUM> to <NUM>%. Further embodiments of the inventive process system can be found with the respective figures and description.

In one embodiment of the process system the first target and the second target are angled in an angle α from a plane in parallel to a substrate plane toward the middle axis Z of a central substrate support, so that the deposition areas of the targets overlap on a substrate surface to be coated. As an example: the angle α can be from <NUM>° to <NUM>°, e.g. <NUM>° ± <NUM>°. The substrate support may comprise means to rotate a disc-shaped substrate stationary centered with axis Z.

In a further embodiment of the inventive process system the first target and the second target are in a sidewise opposite distance D from axis Z' in a plane in parallel to a substrate plane, and the substrate support is of a carousel type and operatively connected to a drive M' to turn substrates circularly round axis z. The control unit can be designed to control the speed of the drive in dependence of a higher sputter power of the first or the second target.

The invention shall now be further exemplified with the help of figures. The figures show:.

<FIG> show schematic concentration profiles which can be applied with inventive coating systems. <FIG> shows a basic scheme applying to all inventive coatings comprising an A<NUM>-xMexN layer, wherein thickness d is the overall thickness of the coating I and along a thickness extent δ3 of said coating a transition layer <NUM> is applied wherein the ratio of atomic percentage of Me to the atomic percentage of A, e.g. xMe/(xA + xMe) multiplied with <NUM> to express a percentage, rises and δ3 ≤ d. The rise in the Me content can be steadily or in small steps, e.g. from steps due to the digitalization from the processing unit. The curve can comprise any curve type from linear (dash-dotted line) to curved (solid line).

A can be at least one of B, Al, Ga, In, Tl.

Me can be one or a combination of two, three or more of the following metals: Mg, Sc, Y, Zr, Nb, Mo, La, Ce, Pr, Nd, Sm Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb. Most commonly it will be Sc or a combination of Sc with one of the metals.

<FIG> shows one variation of <FIG> wherein said Me ratio is constant along a further thickness extent δ2 of said coating, ending at the start of said steadily rising, or to say between the substrate and/or a mere optional adhesion layer (see below) and the transition layer <NUM>, or simply said immediately below the transition layer. Said Me ratio can be zero along said further thickness extent δ2 of said coating, which means that there would be no Me within an AlN of thickness δ2, which is also called a seed layer <NUM>. Layers in parenthesis (<NUM>,. <NUM>) are facultative. A special variation of the coating I comprising a pure AlN seed layer is shown with <FIG>, comprising a concentration-step of the Me-content from the seed layer to the transition layer of the coating. Preferably however at least higher concentration steps should be avoided from the seed-layer to the transition layer and the finalizing top layer <NUM>.

Such a top layer having a further thickness extent δ4 of the coating is shown in <FIG>. The top layer <NUM> starting at the end of said steadily rising transition layer <NUM>. This top layer <NUM> will usually have the highest Me concentration of the coating I.

<FIG> shows two transition layers <NUM> starting at a limiting surface of the coating. The curve on the left showing a transition layer starting directly from the surface of the substrate, the curve on the right showing a transition layer ending at an outer surface towards atmosphere. <FIG> shows a transition layer combining both layers of <FIG>, where the transition layer <NUM> starts with the inner surface of the coating, e.g. directly from the surface of the substrate, from a seed layer or an adhesion layer, and ends at the interface to the top layer <NUM> or the outer surface of the coating. Finally, <FIG> is a special embodiment of <FIG> with the transition layer starting with a Me ratio of zero and ending with the highest concentration. Despite of the fact, that the coating can consist of a transition layer <NUM> only, usually a final top layer of constant high Me concentration will be applied when the piezoelectric response should be increased, and in many cases a pure AlN seed layer will help to provide a more stable base for proper start of crystallization.

An adhesion layer <NUM> which may be beneficial for some type of A<NUM>-xMexN coatings can be applied between the substrate and the seed and/or the transition layer, as an example Mo, W, Pt, Si or a mixture of that elements can be useful. The substrate will be usually silicon which also encompasses partially or fully oxidized surfaces of wafers and alternatively other semiconductors like GaAs.

Further details are given with the following examples.

<FIG> shows an inventive coating I starting from the substrate (S) surface an optional adhesion l layer can be provided directly to the substrates surface, usually followed by a seed layer <NUM> of thickness δ2 directly on the adhesion layer or on the substrate surface if no adhesion layer is used. Adhesion layers as far as electrically conductive may also serve as lower electrode layer for the piezoelectric coating. The seed layer layer may be a pure AN, e.g. AlN or an A<NUM>-xMexN, e.g. Al<NUM>-xMexN layer of low Me, e.g. Sc concentration, e.g. from <NUM> to <NUM> at% or from <NUM> to <NUM> at%. Alternatively, this layer may also consist of a pure AN layer and a respective AMeN layer of low Me concentration, which is shown with a dashed line within seed layer <NUM>. Following directly on the seed layer <NUM> the transition layer <NUM> will follow, usually starting with the same or up to maximum <NUM> atomic% higher Me concentration than the seed layer, e.g. starting without Me (xMe=<NUM>) from a pure AN seed layer and ramping up with Me concentration to the highest Me concentration of the final A1-xMexN, with this example an AMeN top layer with thickness δ4 of constant Me concentration. As an example, the highest Sc concentration in the top layer may be chosen from about <NUM> at% up to <NUM> at% with conventional PVD sputtering like DC, DC-puls or RF technologies. Going to higher concentrations would then inevitably lead to harmful cubic precipitates due to the cubic crystal structure of ScN. However, experiments with the use of HIPIMS-technology, where HIPIMS stand for high power pulsed magnetron, have been performed where even Sc concentrations of up to <NUM>% or even <NUM>% could be deposited in pure or at least highly predominantly hexagonal phase.

It should be mentioned that the top layer need not necessarily end with its outer surface at atmosphere. Further layers known from the state of the art, as for instance a metallic upper electrode layer for the piezoelectric coating and/or scratch or moisture resistant layers, may be provided additionally.

<FIG> displays an exemplary process scheme to apply an inventive coating consisting of a seed layer, a transition layer and a top layer, e.g. in a sputter chamber II as described in detail with <FIG>. The seed layer is deposited with constant sputter power PA (PAl) of the A target (e.g. Al-target) supply during time-span t2 to deposit a pure AN layer, followed by time-span t3 to deposit a AMeN transition layer by ramping up sputter power PMe (PSc) of a supply for a pure Me-target (e.g. Sc) or an AMe-target of high Me concentration, e.g. more than 30at%. In this case a linear ramp is shown. Alternative ramps can be applied to produce concentration curves as shown in <FIG>. In a further alternative process power PA' (PAl') can be reduced by ramping down during at least a part of time-span <NUM> (dash-dotted line), which can be useful especially when AMe-Targets instead of pure Me-targets are used. Finally, the top layer with high Me concentration is deposited with constant power PMe during time-span t3. In general coating composition of the top layer should be the same as at the end of the transition layer. Therefore, deposition parameters can be the same, at least as far the top layer is deposited within the same process module, e.g. within the MMS-chamber by co-sputtering as shown in <FIG>. When the substrate is transferred to a further sputter chamber, e.g. to deposit the top-layer with a higher deposition rate, parameters have to be adapted to meet about the same coating features as with the last sublayer of the transition layer. With the present example reactive gas flow as well as inert gas flow is kept constant during the whole process. Due to a surplus of reactive gas a coating comprising at least approximately or fully stoichiometric reacted AN- respectively A-xMexN-layers can be deposited. Otherwise one, e.g. reactive gas or inert gas, or more, e.g. for both or more types of gas, respective gas ramps can be foreseen to achieve a preferable degree of reaction. An optional adhesion layer <NUM>, e.g. from Mo, Pt, W and/or Si, can be applied during time span t1, instead of applying seed layer <NUM> directly to the substrate surface and a further concentration ramp could be applied between layers <NUM> and <NUM> by providing at least one respective target power ramp over time, not shown.

Table <NUM> refers to process parameters and useful ranges which can be applied with an inventive coating. All experiments were performed in a multisource sputter (MSS) chamber II, see <FIG>, of a respective process module <NUM> of an Evatec Clusterline CLN200 MSQ vacuum system as shown in <FIG>. An Al-target and a Sc-target were arranged in pairwise opposite position as shown in <FIG> the Al-target was used to produce the seed layer, both targets were used for the following transition and top-layer. In column <NUM> of table <NUM> an example of deposition parameters to deposit a top-layer of an inventive coating according to <FIG>. In this example the top layer comprises a <NUM> thick Al<NUM>Sc<NUM>N material, the seed layer comprises <NUM> of pure AlN and a transition layer of, e.g. <NUM> thickness, which starts with zero Scandium to end with a Sc-concentration of <NUM> at% of the top-layer. In column <NUM> and <NUM> process range <NUM> and process range <NUM> are given. Whereat range <NUM> one comprises also process ranges for all other Me-elements, like Lanthanides and other 3b to 6b metals or non-metallic X-elements as mentioned above, range <NUM> comprises parameter ranges to achieve optimized results with reference to piezoelectric features of the coating, e.g. with reference coatings comprising AlScN.

Lower parameter values of range <NUM> or <NUM> may refer to the beginning of the Me-ramp, e.g. of pulsed DC power Scandium, nitrogen gas flow.

Table <NUM> lists in column <NUM> the layer thicknesses of the <NUM> thick coating example as mentioned above and respective thickness ranges <NUM> and <NUM> in columns <NUM> and <NUM>.

<FIG> both show AFM-surface scans as taken with a Park NX20 device (model year <NUM>) wherein the following parameters and AFM-tip were applied.

The AFM-surface scan of <FIG> shows a <NUM> x <NUM> surface area from an AlN seed layer <NUM> of <NUM> thickness which has been deposited within deposition time t2 = <NUM> with constant pulsed DC power (PAl = <NUM> W) and constant parameters as mentioned in table <NUM>, with the exception of power PSc which was zero of course. The seed layer <NUM> was applied directly to a silicon wafer S, no seed layer was applied. Z-axis is in nanometers, color change from light grey (originally brown) to white is about at <NUM>. A so called "spike-analysis" of the surface gave a number of about <NUM> white colored spike tips corresponding to crystallites in a height range of higher than <NUM>, which is about a factor of three to four or more of the average basic roughness without spikes, here about <NUM>. Such relation of the spike height to average surface roughness without spikes is typically for thin layers up to the lower micrometer thickness range. Such results are neither exiting good nor bad, but usual surface qualities of seed layers as used today. Such number of principally undesirable high spikes which obviously also have an impact on surface roughness, however also to piezoelectric response of the coating, are usually reproduced by the next layer to deposit which usually was a piezoelectric top-layer. Thereby seed layer defects have been directly transcribed or often even been amplified by the growth mechanism of the following top layer.

<FIG> shows a very surprising result of an AFM-surface scan of a <NUM> transition layer <NUM> deposited on a seed layer as from <FIG>. Deposition parameters where the same but additionally power PSc has been ramped from zero to <NUM> W during deposition time of layer <NUM> (t3 = <NUM>) of deposition time ending in a very thin final Al<NUM>SC<NUM>N sublayer. Completely unexpected the surface quality improved dramatically by a factor of nearly three with reference to surface spikes which could be reduced to a number of <NUM> spikes within a comparable <NUM> x <NUM> surface area.

Such findings where further validated as can be seen with exemplary time variation parameter sets resulting in a double layer arrangement of different layer thickness and overall coating thickness, both shown in <FIG>. Overall layer thickness DI is growing from <NUM>, <NUM> to <NUM> with reference to the x-coordinate from left to right, whereas in direction of the z-coordinate layer thickness of the transition layer is growing in <NUM> steps from <NUM> to <NUM>, whereas thickness of the seed layer is shrinking from <NUM> to <NUM>. AFM-scans of respective surface areas together with respective so called "spike-numbers" of the spike-analysis are shown in <FIG>. Therewith it could be shown that best results can be achieved with relatively thin seed layers <NUM>, which should be equal or even below <NUM>, i.e. according to the invention from <NUM> to <NUM>, or <NUM> to <NUM>. Whereas thickness of transition layer <NUM> should be preferably equal or higher than the thickness of the seed layer <NUM>, i.e. according to the invention from <NUM> to <NUM>, e.g. from <NUM> to <NUM>.

<FIG> shows schematically a multisource sputter (MSS) chamber II of an inventive process system III. The MSS chamber comprises a <NUM>st target <NUM> made from A and a <NUM>nd target <NUM> made from Me or AMe to stick with the examples above. Alternatively, the <NUM>nd target can be made from any of the metals as mentioned above or from respective AMe alloys, e.g. metallurgically manufactured, or AMe mixtures, e.g. from powder metallurgically produced targets. Targets <NUM>, <NUM> are powered via lines <NUM>, <NUM> by a respective <NUM>st power supply <NUM> and <NUM>nd power supply <NUM>. The <NUM>st and/or <NUM>nd power supply can be a DC, a pulsed DC, a DC superimposed with a pulsed DC, a DC superimposed with a RF, or a HIPIMS-supply. The target substrate distance is defined according to <FIG> from the middle of the targets which are angled, here with an angle α of about <NUM>° from a plane in parallel to a substrate plane <NUM> toward the middle of the substrate S and chamber axis Z, and can be chosen according to table <NUM>. Thereby deposition areas of up to four targets, e.g. <NUM> A targets and <NUM> Me targets, overlap a major part or the whole area of the substrate surface, that is <NUM>% to <NUM>%, preferably <NUM>% to <NUM>% of the substrate area. Overlapping hereby refers to a sputter cone originating from the outer boarder of the active target surface, that is the sputtered surface, with an opening angle of about <NUM>° from the target axes. Rotatable mounting of the sputter sources round central axis Z in an upper region of the MSS-chamber and/or, e.g. opposite substrate rotation, and/or rotation round target axes T<NUM>, T<NUM> (both symbolized by respective circular double arrows) may further foster even material distribution and layer quality. The substrate is supported by a substrate holder <NUM>, e.g. a chuck, which will usually comprise heating and/or cooling means. The chuck <NUM> can be an ESC chuck to fix a flat substrate safely. The disc-shaped substrate, e.g. a wafer, which is centered with axis Z, can be rotated stationary by drive M. It should be mentioned that angle α may vary from <NUM>° up to <NUM>° up to the actual distance TS, speed of substrate rotation and/or target rotation and facultatively further geometric parameters. The chamber is pumped by a high vacuum pumpsystem P comprising respective pump lines, a high vacuum pump and at least one forepump or roughpump. Present parameters are optimized to a chamber for <NUM> flat round substrates like wafers and circular <NUM> targets. Up-scaling and down-scaling procedures are known to the man of the art. With such an MSS-chamber, which can be equipped with two or four targets circularly arranged in respective pairwise opposite position as shown in <FIG>, all process steps to deposit as mentioned inventive coatings can be performed, even adhesion coatings can be performed if at least one of the sputter stations is equipped with respective target material. Such multipurpose use of the MSS-chamber II however obviously results in longer process cycles compared to an MCS system as described in the following.

<FIG> shows schematically an alternative multisource sputter (MSS) chamber II' which could be used instead of chamber II with an inventive process system III. With a chamber II' a plurality of substrates <NUM> can be coated at the same time with seed layer <NUM>, transition layer <NUM> or top-layer <NUM> according to the respectively chosen coating parameters. Again chamber II' comprises at least one <NUM>st target <NUM> made from A and at least one <NUM>nd target <NUM> made from Me or AMe. As with chamber II targets of different material A or Me respectively AMe are arranged in alternating sequence when two, four, six or more targets are mounted. With this embodiment however targets are arranged along a circular path above and in parallel to a substrate support <NUM>', respectively the surface of the substrates <NUM>. Substrate support <NUM>' is of a carousel type, driven by drive M', turning the substrates circularly round axis Z and will usually have additional drives M to rotate substrates round planetary axes Z. Similar rotation (only "planetary" and/or circularly) can be foreseen with the targets <NUM>, <NUM>, respectively the corresponding magnetic systems or the sputter sources as a whole (not shown). With reference to target material, sputter power, target to substrate distance, and use for deposition of different layers it can be referred to the respective remarks as mentioned above. Only with the deposition of a gradient layer <NUM> and a top-layer <NUM> it should be mentioned that due to the separate deposition areas which have no or at least less overlapping of the target cones compared to the confocally arranged angled targets in chamber II, the rotation of the carousel <NUM>' and where applicable a counterrotation of the targets <NUM>, <NUM> round axis Z has to be fast enough that only very thin sublayers of one or only a few atomic layers are deposited when the substrates pass by the targets. Thereby the minimum rotation speed depends primarily from the sputter power of the target(s) with the higher sputter rate which can be the first or the second target(s) depending on the respective Me/(A+Me) ratio to be deposited. Providing such thin layers in rapid sequence, atomic mixing or alloying of the AN and MeN or AMeN sublayers can be achieved and thereby similar material properties can be provided as with overlapping sputter cones as discussed above.

Targets with all embodiments of the invention can be magnetron targets. For a better layer distribution a planetary rotation of the targets, or of at least parts of the magnetic system of the targets, can be foreseen, e.g. round axis T10, T11 or an axis encompassing supply lines <NUM>', <NUM>'.

A vacuum process system to produce inventive piezoelectric coatings in an industrial scale is shown in <FIG>. substrates S are transferred into ↑ and out of ↓ the system vacuum via load-lock chambers <NUM>, <NUM> and placed into six pre- and postprocessing modules <NUM>, <NUM>', <NUM>, <NUM>' which are pairwise positioned above and below a wafer handling level. Further on the system comprises six process modules <NUM> to <NUM>. All modules <NUM> to <NUM> are arranged circular or polygonal round a central handler compartment <NUM> comprising a freely programmable handler <NUM> to transfer ↕ ↔ wafers S from a pre-processing <NUM> module to processing modules <NUM> to <NUM>, transfer wafers between modules, and finally transfer back the wafer to a post-processing tool <NUM>. Transfer in and out of the multi chamber vacuum process system (MCS) is done by a load-lock <NUM> for incoming wafers and a load-lock <NUM> for outgoing wafers. At least one further handler (not shown) transfers wafers from the load-lock chamber(s) <NUM>, <NUM>, here realized as one load lock section, to a preprocessing module <NUM> and back again to the load-lock section from postprocessing module <NUM>. Pre- and postprocessing modules <NUM>, <NUM>' and <NUM>, <NUM>' may comprise at least one of a buffer for wafers waiting to be processed or transferred, a heating station, a cooling station, an etching station and an aligner station. Module <NUM> may comprise an etching station to etch substrates before or between sputter deposition is performed in further processing modules to tailor the overall process in the MCS. Modules <NUM> and <NUM> comprise at least on metal-sputter station each equipped with a Mo-target, respectively a Pt-target to apply an adhesion layer on the substrate surface which gives the operator the possibility to choose if necessary the most adequate adhesion coating for different substrate types or surface conditions. Module <NUM> may comprise a metal-sputter station, equipped with an A-target to apply, e.g. an AN seed layer within a short period of time. Module <NUM> may comprise a metal-sputter station, equipped with an AMe-target, e.g. an AlSc-target, to apply a final relatively thick AMeN, e.g. AlScN layer. In another MCS arrangement, even two process modules, e.g. module <NUM> and <NUM> may be equipped with respective targets to split the last layer deposition process and thereby speed up production cycle.

A system control unit <NUM> of the MCS, which may include the respective system units of the modules or a least control the timing of such units, controls wafer transfer as well as process details within every module by control and/or adjusting means <NUM>, measurement means and sensors (not shown) which again may be included at least in part within the system control unit <NUM> or separate with respective modules to be controlled. An input/output unit <NUM> allows an operator to modify single process parameters and to load new processes automatically. With the vacuum process system as shown, every processing module is pumped by a high vacuum pump system P and so can be the central handler compartment <NUM>, the preprocessing module <NUM>, the postprocessing module <NUM>, and/or load lock chambers <NUM>, <NUM>. Finally, it should be mentioned that a combination of features mentioned with one embodiment, examples or types of the present invention can be combined with any other embodiment, example or type of the invention as defined by the claims unless being in contradiction.

Claim 1:
A substrate having a surface coated with a piezoelectric coating (I), the coating comprising A<NUM>-xMexN, wherein A is at least one of B, Al, Ga, In, Tl, and Me is at least one metallic element from the transition metal groups 3b, 4b, 5b, 6b, the lanthanides, and Mg, the coating (I) having a thickness d, and further comprising a transition layer (<NUM>) wherein starting from the substrate side a ratio of an atomic percentage of Me to an atomic percentage of A steadily rises along a thickness extent δ3 of said coating for which there is valid: <MAT>
wherein the coating further comprises a seed-layer (<NUM>) ending at the start of said steadily rising of the transition layer (<NUM>), wherein said ratio is constant along a thickness extent δ2 of the seed-layer;
wherein a thickness of the transition layer (<NUM>) is equal or higher than the thickness of the seed layer (<NUM>), the thickness of the transition layer (<NUM>) being from <NUM> to <NUM> and the thickness of the seed layer being from <NUM> to <NUM>;
so that the surface of the transition layer (<NUM>) has a uniform surface quality of less than <NUM> spikes in any <NUM> x <NUM> surface area.