Patent Description:
Embodiments of the present disclosure generally relate to bismuth antimony (BiSb) alloys with (<NUM>) orientation for use as topological insulators.

BiSb with (<NUM>) orientation is a narrow gap topological insulator with both giant spin Hall effect and high electrical conductivity. BiSb is a material that has been proposed in various spin-orbit torque (SOT) applications, such as for a spin Hall layer for magnetoresistive random access memory (MRAM) devices and energy-assisted magnetic recording (EAMR) write heads.

However, BiSb materials have yet to be adopted in commercial SOT applications due to several obstacles. For example, BiSb materials have low melting points, large grain sizes, significant Sb migration issues upon thermal annealing due to its film roughness, difficulty maintaining a (<NUM>) orientation for maximum spin Hall effect and are generally soft and easily damaged by ion milling.

Therefore, there is a need for an improved SOT device and process of forming a BiSb layer with (<NUM>) orientation.

The invention is a device as defined in the appended independent claim <NUM>. Embodiments of the present invention generally relate to bismuth antimony (BiSb) alloys with (<NUM>) orientation for use as topological insulators in spin-orbit torque (SOT) devices as defined by the subject matter of the claims.

<CIT> describes voltage-controlled magnetic based devices that include a magnetic insulator; a topological insulator adjacent the magnetic insulator; and magnetic dopants within the topological insulator. The magnetic dopants are located within an edge region of the topological insulator to inhibit charge current flow in the topological insulator during a switching operation using an applied electric field generating by applying a switching voltage across two electrodes at opposite sides of the topological insulator. Power dissipation due to carrier-based currents can be avoided or at least minimized by the magnetic dopants at the edges of the topological insulator.

<NPL>), spin-orbit torque switching using the spin Hall effect in heavy metals and topological insulators.

In an article entitled "<NPL> et al. review the basic concepts of magnetic topological insulators and their experimental realization, together with the discovery and verification of their emergent properties. In particular, they discuss how the development of tailored materials through heterostructure engineering has made it possible to access the quantum anomalous Hall effect, the topological magnetoelectric effect, the physics related to the chiral edge states that appear in these materials and various spintronic phenomena.

So that the manner in which the above-recited features of the present disclosure can be understood in detail, a more particular description of the disclosure, briefly summarized above, may be had by reference to examples, some of which are illustrated in the appended drawings. It is to be noted, however, that the appended drawings illustrate only typical embodiments of this invention and examples and are therefore not to be considered limiting of its scope, for the invention may admit to other equally effective embodiments.

It is contemplated that elements disclosed in one example may be beneficially utilized on other examples without specific recitation.

In the following, reference is made to embodiments of the invention and examples. However, it should be understood that the invention is not limited to specific Thus, the following aspects, features, embodiments and advantages are merely illustrative and are not considered elements or limitations of the appended claims except where explicitly recited in a claim(s). Likewise, a reference to "the disclosure" shall not be construed as a generalization of any inventive subject matter disclosed herein and shall not be considered to be an element or limitation of the appended claims except where explicitly recited in a claim(s). Usage in the Summary of the invention or in the Detailed Description of the term "comprising" shall mean comprising, consisting essentially, and/or consisting of.

Embodiments of the present invention generally relate to bismuth antimony (BiSb) alloys with (<NUM>) orientation for use as topological insulators as defined by the subject matter of the claims. The BiSb alloys comprise bismuth, antimony, and a dopant element (E) and are herein referred to as BiSbE alloys. The dopant element comprises a non-metallic dopant element, a metallic dopant element, or combinations thereof.

BiSbE alloy layers with (<NUM>) orientation have a large spin Hall angle effect and high electrical conductivity. Certain embodiments of the BiSbE alloy layers have reduced grain size and lower interfacial roughness in comparison to a BiSb material without dopant elements. Certain embodiments of the BiSbE alloy layers comprising a metallic dopant element have an increased melting temperature and allow higher annealing temperatures to be used while maintaining high (<NUM>) texture in comparison to a BiSb material without dopant elements. BiSbE alloy layers having (<NUM>) orientation can be used to form spin-orbit torque (SOT) devices, such as spin Hall electrode layers in MRAM devices or in an EAMR write heads. For example, BiSbE alloy layers are implemented into the manufacturing of SOT devices which are annealed to set magnetic directions of perpendicular magnetic anisotropy (PMA) ferromagnetic layers.

A prior BiSb layer with (<NUM>) orientation has a large spin Hall angle effect and high electrical conductivity. TABLE <NUM> shows one example of the properties of a BiSb layer with (<NUM>) orientation in comparison to beta-tantalum and to a BiSb layer with (<NUM>) orientation. A BiSb layer with (<NUM>) orientation has similar electrical conductivity and a much larger spin Hall angle than beta-tantalum (Beta-Ta) or a BiSb layer with (<NUM>) orientation. Therefore, the relative power required to produce a spin Hall effect is lower for BiSb (<NUM>) in comparison to Beta-Ta or BiSb (<NUM>).

Prior BiSb materials with Sb content from about <NUM> atomic % to about <NUM> atomic % have melting points from about <NUM> to about <NUM> depending on the Sb content. During annealing, prior BiSb materials experience high levels of undesirable Sb migration due to the high roughness of the BiSb materials.

The present BiSbE alloy layers according to various embodiments disclosed herein have a high degree of (<NUM>) orientation, a large spin Hall angle effect, a low interfacial roughness, and a high electrical conductivity comparable to BiSb (<NUM>) materials without dopant elements. In certain embodiments, the BiSbE alloy layers with metallic dopant elements provide higher annealing temperatures to be used in comparison to BiSb materials without dopant elements.

In certain embodiments, a BiSbE alloy layer includes a non-metallic dopant element comprising Si, P, Ge, other suitable non-metallic dopant elements, or combinations thereof. In certain embodiments, a BiSbE alloy layer includes a metallic dopant element comprising Ni, Co, Fe, CoFe, NiFe, NiCo, NiCu, CoCu, NiAg, CuAg, Cu, Al, Zn, Ag, Ga, In, other suitable metallic dopant elements, or combinations thereof.

In certain embodiments, a BiSbE alloy layer comprises Bi<NUM>-xSbxE wherein x is <NUM> < x < <NUM> and comprises the dopant element (E) from about <NUM> atomic % to about <NUM> atomic %.

Without being bound by theory unless specifically set forth in the claims, it is believed that the dopant element of the BiSbE alloy layer has a low solubility inside the BiSb lattice while maintaining the topological insulator property and the (<NUM>) orientation of the BiSb material. It is believed that a portion of the dopant element goes into the BiSb lattice after deposition. For example, in certain embodiments for a dopant element deposited at room temperature, a portion of the dopant element goes into the BiSb lattice and contracts the a-axis by about <NUM>% and expands the c-axis from about <NUM> to about <NUM>%. It is believed that a portion of the dopant element can act as a grain boundary segregant refining the structure of the BiSb grains or go to the BiSbE interfacial regions forming part of a seed layer or part of a cap layer.

<FIG> is a schematic illustration of a top down planar view of a BiSbE alloy layer <NUM> at deposition. The BiSbE alloy layer <NUM> comprises a plurality of BiSb lamellae layers <NUM> and one or more dopant element lamellae layers at deposition. The BiSbE alloy layer <NUM> comprises grains of BiSb and a layer of atoms/clusters <NUM> of dopant element(s) deposited uniformly over the grains of BiSb. It is believed that the atoms/clusters <NUM> of dopant element lamella layer forms uniformly over the BiSb lamella layer <NUM>.

<FIG> is a schematic illustration of a top down planar view of the BiSbE alloy layer <NUM> after post annealing. It is believed that the atoms/clusters <NUM> of dopant element(s) have been redistributed to the grain boundaries of the BiSbE lamella layer <NUM>. Some portion of the atoms/clusters <NUM> of dopant element is retained in the BiSb lattice while another portion of the atoms/clusters <NUM> of dopant element goes to the grain boundaries of the BiSb and to the BiSbE interfaces. The portion of the dopant element that goes to the grain boundaries of the BiSb becomes a segregant which reduces the grain size of the BiSb and reduces the interfacial roughness of the BiSbE alloy layer <NUM>. In certain embodiments, the portion of the dopant element comprising metallic dopant elements that is retained in the BiSb lattice increases the melting point of the BiSbE alloy layer in comparison to a BiSb layer without dopant elements. The portion of the dopant element that is retained in the BiSb lattice allows the annealing temperature of the BiSbE alloy layer to be increased due to alloying (lattice hardening) and grain boundary segregation (grain size hardening) effects which pin and restrict the grain boundaries from moving at elevated temperatures. The BiSbE alloy layer is able to withstand an anneal, such as an anneal of about <NUM> or above for three hours or more.

<FIG> is a schematic illustration of a cross-sectional layer view of the BiSbE alloy layer <NUM> after post annealing. It is believed that the atoms/clusters <NUM> of dopant element(s) have been redistributed to the grain boundaries of the BiSbE lamella layer <NUM> and to seed or cap layer interfaces, such as a silicide seed or silicide cap layer interfaces. The portion of the dopant element that goes to the grain boundaries becomes the segregant which reduces or modifies the grain size and lattice parameters of the grains <NUM> of BiSb and reduces the interfacial roughness of the BiSbE alloy layer <NUM>.

In certain embodiments, the interfacial roughness of the BiSbE alloy layer with a silicide seed layer and with a silicide cap layer is about <NUM>Å or less. In certain embodiments, interfacial roughness of the BiSbE alloy layer with a silicide seed layer and a silicide cap layer is reduced by about from about <NUM>Å to about <NUM>Å in comparison to a BiSb material without dopant elements. The use of a metal interlayers between the BiSbE alloy layer and the silicide seed layer and between the BiSbE alloy layer and the silicide cap layer further reduces the interfacial roughness for the BiSbE alloy layer.

The (<NUM>) texture is enhanced with a BiSbE alloy layer in comparison to a BiSb without dopant elements. For example, in certain embodiments, the (<NUM>) texture of a BiSbE alloy stack of a silicide seed layer, a metal interlayer, a BiSbE alloy layer, a metal interlayer, a silicide cap layer has a rocking curve with widths less than <NUM> degrees, such as from about <NUM> to about <NUM> degrees. In comparison, the (<NUM>) texture of a BiSb stack without dopant elements of a stack of a silicide seed layer, a metal interlayer, a BiSb layer, a metal interlayer, a silicide cap layer has a rocking curve with widths of about <NUM> degrees or more and with a dual (<NUM>) and (<NUM>) texture.

In certain embodiments, the BiSbE alloy layer is formed to a thickness from about <NUM>Å to about <NUM>Å, such as from about <NUM>Å to about <NUM>Å. In other embodiments, the BiSbE alloy layer is formed to any suitable thickness. In certain embodiments, the BiSbE alloy layer is deposited by physical vapor deposition (PVD), such as sputtering, molecular beam epitaxy, ion beam deposition, other suitable PVD processes, and combinations thereof. In certain embodiments, a SOT device includes a BiSbE alloy layer formed over any suitable layer and with any suitable layer formed over the BiSbE alloy layer.

In embodiments, the BiSbE alloy layer comprises a multi-layer laminate of a plurality of BiSb lamellae layers and one or more dopant element lamellae layers. The BiSbE alloy multi-layer laminate provides placement of the dopant element lamella layer at specific regions of the BiSbE alloy layer to increase nucleation and growth of (<NUM>) orientation, to reduce interfacial roughness, and/or to reduce grain size.

In one embodiment, the BiSbE alloy layer comprises <NUM> to <NUM> BiSb lamellae layers with each BiSb lamella layer having a thickness from about <NUM>Å to about <NUM>Å and comprises <NUM> to <NUM> dopant element lamellae layers with each dopant element lamella layer having a thickness from about <NUM>Å to about <NUM>Å. One or more dopant element lamellae layers are interspersed between the BiSb lamellae layers. In other embodiments, the BiSbE alloy layer comprises any suitable number of BiSb lamellae layers with each BiSb lamella layer formed to any suitable thickness and comprises any suitable number of dopant element lamellae layers with each dopant element lamella layer formed to any suitable thickness.

<FIG> is a schematic illustration of deposition of a BiSbE alloy layer <NUM> comprising six BiSb lamellae layers <NUM> and five dopant element lamellae layers <NUM>. A dopant element lamella layer <NUM> has been deposited between each of the BiSb lamellae layers <NUM>. The dopant element lamellae layers <NUM> have been deposited throughout the BiSbE alloy layer <NUM>. <FIG> is a schematic illustration of the distribution of the dopant element within the BiSb lamellae layers <NUM> of the BiSbE alloy layer <NUM> at deposition or after annealing. The dopant element is distributed into each of the BiSb lamellae layers <NUM>.

<FIG> is a schematic illustration of deposition of a BiSbE alloy layer <NUM> comprising six BiSb lamellae layers <NUM> and four dopant element lamellae layers <NUM>. The BiSbE alloy layer <NUM> can also be viewed as two thin BiSb lamellae layers <NUM> at the bottom edge, two thin BiSb lamellae layers <NUM> at the top edge, and a thick BiSb lamella layer 210T at the center with dopant element lamellae layers <NUM> therebetween. The dopant element lamellae layers <NUM> have been deposited at the bottom edge and the top edge of the BiSbE alloy layer <NUM> but not at the center of the BiSbE alloy layer <NUM>. <FIG> is a schematic illustration of the distribution of the dopant element within the BiSb lamellae layers <NUM> of the BiSbE alloy layer <NUM> at deposition or after annealing. The dopant element is distributed at the bottom edge and the top edge of the BiSbE alloy layer <NUM>.

<FIG> is a schematic illustration of deposition of a BiSbE alloy layer <NUM> comprising six BiSb lamellae layers <NUM> and three dopant element lamellae layers <NUM>. The BiSbE alloy layer <NUM> can also be viewed as one thin BiSb lamella layer <NUM> at the bottom edge, one thin BiSb lamella layer <NUM> at the top edge, and two thick BiSb lamellae layers 210T at the center with dopant element lamellae layers <NUM> therebetween. The dopant element lamellae layers <NUM> have been deposited every other BiSb lamella layer <NUM>. The dopant element lamellae layers <NUM> have been deposited at the bottom edge, the center, and the top edge of the BiSbE alloy layer <NUM>. <FIG> is a schematic illustration of the distribution of the dopant element within the BiSb lamellae layers <NUM> of the BiSbE alloy layer <NUM> at deposition or after annealing. The dopant element is distributed at the bottom edge, the center, and the top edge of the BiSbE alloy layer <NUM>.

<FIG> is a schematic illustration of deposition of a BiSbE alloy layer <NUM> comprising six BiSb lamellae layers <NUM> and three dopant element lamellae layers <NUM>. The BiSbE alloy layer <NUM> can be viewed as three thin BiSb lamellae layers <NUM> at the bottom edge and one thick BiSb lamella layer 210T at top edge with dopant element lamellae layers <NUM> therebetween. The dopant element lamellae layers <NUM> have been deposited at the bottom edge but not at the top edge of the BiSbE alloy layer <NUM>. <FIG> is a schematic illustration of the distribution of the dopant element within the BiSb lamellae layers <NUM> of the BiSbE alloy layer <NUM> at deposition or after annealing. The dopant element is distributed at the bottom edge of the BiSbE alloy layer <NUM>.

<FIG> is a schematic cross-sectional view of certain embodiments of a SOT device <NUM> having a BiSbE alloy layer <NUM> with (<NUM>) orientation forming a SOT-based magnetoresistive random access memory (MRAM) device as defined by the subject matter of the claims.

The BiSbE alloy layer <NUM> with (<NUM>) orientation is formed over a substrate <NUM>, such as a silicon substrate, an alumina substrate, or other suitable substrates. A seed layer <NUM> is deposited over the substrate <NUM>. The seed layer <NUM> comprises a silicide layer <NUM> or other suitable seed layers. In certain embodiments, the silicide layer <NUM> comprises NiSi, NiFeSi, NiFeTaSi, NiCuSi, CoSi, CoFeSi, CoFeTaSi, CoCuSi, or combinations thereof. In certain embodiments, the seed layer <NUM> further comprises a surface control layer <NUM> between the silicide layer <NUM> and the BiSbE alloy layer <NUM>. In certain embodiments, the surface control layer <NUM> comprises NiFe, NiFeTa, NiTa, NiW, NiFeW, NiCu, NiFeCu, CoTa, CoFeTa, NiCoTa, Co, CoM, CoNiM, CoNi, NiSi, CoSi, NiCoSi, Cu, CuAg, CuAgM, CuM, or combinations thereof, in which M is Fe, Cu, Co, Ta, Ag, Ni, Mn, Cr, V, Ti, or Si.

In certain embodiments, an interlayer <NUM> is deposited over the BiSbE alloy layer <NUM>. The interlayer <NUM> comprises a silicide layer <NUM>. In certain embodiments, the silicide layer <NUM> comprises NiSi, FeSi, CoSi, NiCuSi, NiFeTaSi, CoFeSi, CoCuSi, or combinations thereof. In certain embodiments, the interlayer <NUM> further comprises a surface control layer <NUM> between the BiSbE alloy layer <NUM> and the silicide layer <NUM>. The surface control layer <NUM> comprises Cu, Ni, NiFe, Co, or combinations thereof.

A free perpendicular magnetic anisotropy (PMA) layer <NUM> is formed over the interlayer <NUM>. For example, the free PMA layer <NUM> can comprise one or more stacks of a Co/Pt, Co/Pd, Co/Ni, CoFeB, FePt or other PMA inducing layers or combinations thereof. An insulating layer <NUM>, such as a MgO layer, is formed over the free PMA layer <NUM>. A reference PMA layer <NUM> is formed over the insulating layer <NUM>. The reference PMA layer <NUM> can comprise one or more stacks of a Co/Pt, Co/Pd, Co/Ni, CoFeB, FePt or other PMA inducing layers or combinations thereof. The reference PMA layer <NUM> can include one or more synthetic antiferromagnetic (SAF) pinned structures. A cap layer <NUM> can be formed over the reference PMA layer <NUM>. The cap layer <NUM> comprises NiFe, SiN, Si, NiFeTa, NiTa, Pt, Co, Cu, Ni, NiCu, CoCu, Ru, Ta, Cr, Au, Rh, CoFe, CoFeB, other non-magnetic materials, other magnetic materials, and combinations thereof. The magnetic direction of the reference PMA layer <NUM> can be set with an anneal of about <NUM> or above for two hours or more. In certain embodiment, the BiSbE alloy layer <NUM> comprises a metallic dopant element. The metallic dopant element of the BiSbE alloy layer <NUM> helps to maintain the low interfacial roughness of the BiSbE alloy layer <NUM> after anneal and helps to the manufacturability, performance, and/or life time of the MRAM device. The BiSbE alloy layer <NUM> comprises a metallic dopant element has reduced migration of Sb of the BiSbE alloy layer <NUM> after post annealing in comparison to a BiSb material without dopant elements.

A plurality of the SOT devices <NUM> can be configured together as part of a memory cell array in which the BiSbE alloy layer <NUM> is a spin orbit material electrode. A top electrode (not shown) can be disposed over the reference PMA layer <NUM>. Each of the memory cells may be part of a two-terminal device or a three terminal device. The spin orbit material electrode and the top electrode may serve as bit lines, word lines, read word lines, write word lines, and combinations thereof. The memory cell array may be implemented as a crosspoint array or other architectures.

<FIG> is a schematic cross-sectional view of certain embodiments of a SOT device <NUM> having a BiSbE alloy layer <NUM> with (<NUM>) orientation forming a portion or component of a SOT-based EAMR write head used in magnetic recording as defined by the subject matter of the claims.

A spin-torque layer (STL) <NUM> is formed over the interlayer <NUM>. The STL <NUM> comprises a ferromagnetic material such as one or more layers of CoFe, Colr, NiFe, and CoFeM wherein M = B, Ta, Re, or Ir. Charge current through a BiSbE alloy layer <NUM> acting as a spin Hall layer generates a spin current in the BiSbE layer <NUM>. The spin-orbital coupling of the BiSbE alloy layer <NUM> and a spin torque layer (STL) <NUM> causes switching or precession of magnetization of the STL <NUM> by the spin-orbital coupling of the spin current from the BiSbE alloy layer <NUM>. Switching or precession of the magnetization of the STL <NUM> can generate an assisting DC field to the write field from a main pole of a write head used in magnetic recording. SOT based EAMR elements have multiple times greater power efficiency in comparison to spin-transfer torque (STT) based Microwave-Assisted Magnetic Recording (MAMR) elements. In an embodiment, the BiSbE alloy layer <NUM> comprises a metallic dopant element or a non-metallic dopant element. For example, if the SOT-based EAMR write head is not annealed, a BiSbE alloy layer <NUM> comprising a non-metallic dopant element can be used since degradation of the interfacial roughness due to post annealing is avoided.

A SOT device includes a bismuth antimony dopant element (BiSbE) alloy layer over a substrate. The BiSbE alloy layer is used as a topological insulator, such as for SOT-based MRAM device or for SOT-based EAMR write head. The BiSbE alloy layer includes bismuth, antimony, a dopant element. The dopant element can be a non-metallic dopant element comprising Si, P, Ge, or combinations thereof, a metallic dopant element comprising Ni, Co, Fe, CoFe, NiFe, Cu, Al, Zn, Ag, Ga, In, or combinations thereof, or a combination of a non-metallic dopant element(s) and a metallic dopant element(s). The BiSbE alloy layer can include a plurality of BiSb lamellae layers and one or more dopant element lamellae layers. The BiSbE alloy layer has a (<NUM>) orientation. In certain embodiments, the BiSbE alloy layer has a higher annealing temperature, stronger (<NUM>) texture, smaller grain size, and/or lower surface roughness in comparison to a BiSb material without dopant elements.

In one example, a SOT device includes a bismuth antimony dopant element (BiSbE) alloy layer over a substrate. The BiSbE alloy layer includes bismuth, antimony, and a dopant element. The dopant element is a non-metallic dopant element, a metallic dopant element, and combinations thereof. Examples of metallic dopant elements include Ni, Co, Fe, CoFe, NiFe, NiCo, NiCu, CoCu, NiAg, CuAg, Cu, Al, Zn, Ag, Ga, In, or combinations thereof. Examples of non-metallic dopant elements include Si, P, Ge, or combinations thereof. The BiSbE alloy layer has a (<NUM>) orientation.

In another example, a SOT device includes a bismuth antimony dopant element (BiSbE) alloy layer over a substrate. The BiSbE alloy layer includes a plurality of BiSb lamellae layers and one or more dopant element lamellae layers. Each of the dopant element lamellae layers includes a non-metallic dopant element, a metallic dopant element, and combinations thereof. Examples of metallic dopant elements include Ni, Co, Fe, CoFe, NiFe, NiCo, NiCu, CoCu, NiAg, CuAg, Cu, Al, Zn, Ag, Ga, In, or combinations thereof. Examples of non-metallic dopant elements include Si, P, Ge, or combinations thereof. The BiSbE alloy layer has a (<NUM>) orientation.

In still another example, a magnetoresistive random access memory (MRAM) device includes a bismuth antimony dopant element (BiSbE) alloy layer. The BiSbE alloy layer includes bismuth, antimony, and a metallic dopant element. The metallic dopant element is Ni, Co, Fe, CoFe, NiFe, NiCo, NiCu, CoCu, NiAg, CuAg, Cu, Al, Zn, Ag, Ga, In, or combinations thereof. The BiSbE alloy layer having a (<NUM>) orientation. The MRAM device further includes a perpendicular magnetic anisotropy (PMA) ferromagnetic layer.

The following are examples to illustrate various embodiments of a BiSbE alloy layer <NUM>, <NUM>, <NUM> of <FIG>, <FIG>, or <FIG>, other SOT devices, and variations thereof. These examples are not meant to limit the scope of the claims unless specifically recited in the claims.

<FIG> shows <NUM>-theta XRD scans vs. logarithm of the intensity of the BiSb orientation of various stacks <NUM>-<NUM> of BiSbE alloy layers comprising a non-metallic dopant element of Si. Each of the stacks <NUM>-<NUM> comprised a seed layer of a NiFeCu-silicide layer formed to a thickness of about <NUM>Å and a copper alloy (CuAgNi) layer formed to a thickness of about <NUM>Å, a BiSbE alloy layer formed to a thickness of about <NUM>Å, an interlayer of a NiFe-silicide layer formed to a thickness of about <NUM>Å, and a cap layer of SiN formed to a thickness of <NUM>Å. The BiSbSi alloy layers comprised a plurality of BiSb lamellae layers and a plurality of Si lamellae layers in which the dopant element comprised Si. Each of the BiSb lamellae layers comprised about <NUM> atomic % of Bi and about <NUM> atomic % of Sb.

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three Si lamellae layers with each Si lamella layer deposited to a thickness of about <NUM>Å. The Si lamellae layers were deposited at the top edge of the BiSbE alloy layer in the order of BiSb-BiSb-BiSb-Si-BiSb-Si-BiSb-Si-BiSb (BBBSBSBSB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three Si lamellae layers with each Si lamella layer deposited to a thickness of about <NUM>Å. The Si lamellae layers were deposited at the center of the BiSbE alloy layer in the order of BiSb-BiSb-Si-BiSb-Si-BiSb-Si-BiSb-BiSb (BBSBSBSBB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three Si lamellae layers with each Si lamella layer deposited to a thickness of about <NUM>Å. The Si lamellae layers were deposited at the bottom edge of the BiSbE alloy layer in the order of BiSb-Si-BiSb-Si-BiSb-Si-BiSb-BiSb-BiSb (BSBSBSBBB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three Si lamellae layers with each Si lamella layer deposited to a thickness of about <NUM>Å. The Si lamellae layers were modulated within the BiSbE alloy layer in the order of BiSb-Si-BiSb-BiSb-Si-BiSb-BiSb-Si-BiSb (BSBBSBBSB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing four Si lamellae layers with each Si lamella layer deposited to a thickness of about <NUM>Å. The Si lamellae layers were deposited at the bottom edge and the top edge of the BiSbE alloy layer in the order of BiSb-Si-BiSb-Si-BiSb-BiSb-Si-BiSb-Si-BiSb (BSBSBBSBSB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing five Si lamellae layers with each Si lamella layer deposited to a thickness of about <NUM>Å. The Si lamellae layers were deposited throughout the BiSbE alloy layer in the order of BiSb-Si-BiSb-Si-BiSb-Si-BiSb-Si-BiSb-Si-BiSb (BSBSBSBSBSB).

Stack <NUM> with a top edge distribution of the dopant element Si and stack <NUM> with a center distribution of dopant element Si do not promote strong BiSbSi (<NUM>) orientation. Stack <NUM> with a bottom edge distribution of dopant element Si, stack <NUM> with a modulated distribution of dopant element Si, stack <NUM> with a bottom edge and top edge distribution of dopant element Si, and stack <NUM> with a dopant element Si distribution the throughout the BiSbE alloy layer promoted strong BiSbSi(<NUM>) orientation.

<FIG> shows <NUM>-theta XRD scans vs. logarithm of the intensity of the BiSb orientation of various stacks <NUM>-<NUM> of BiSbE alloy layers comprising a metallic dopant element of CuAgNi. The BiSbE alloy layers comprised a plurality of BiSb lamellae layers and a plurality of lamellae layers of metallic dopant element of CuAgNi. Each of the BiSb lamellae layers comprised about <NUM> atomic % of Bi and about <NUM> atomic % of Sb. Each of the stacks <NUM>-<NUM> comprised a seed layer of a NiFeCu-silicide layer formed to a thickness of about <NUM>Å, a BiSbE alloy layer formed to a thickness of about 100Å, an interlayer of a NiFe-silicide layer formed to a thickness of about <NUM>Å, and a cap layer of SiN formed to a thickness of <NUM>Å.

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three CuAgNi lamellae layers with each CuAgNi lamella layer deposited to a thickness of about <NUM>Å. The CuAgNi lamellae layers were deposited at the top edge of the BiSbE alloy layer in the order of BiSb-BiSb-BiSb-CuAgNi-BiSb-CuAgNi-BiSb-CuAgNi-BiSb (BBBCBCBB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three CuAgNi lamellae layers with each CuAgNi lamella layer deposited to a thickness of about <NUM>Å. The CuAgNi lamellae layers were deposited at the center of the BiSbE alloy layer in the order of BiSb-BiSb-CuAgNi -BiSb-CuAgNi-BiSb-CuAgNi-BiSb-BiSb (BBCBCBCBB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three CuAgNi lamellae layers with each CuAgNi lamella layer deposited to a thickness of about <NUM>Å. The CuAgNi lamellae layers were deposited at the bottom edge of the BiSbE alloy layer in the order of BiSb-CuAgNi -BiSb-CuAgNi-BiSb-CuAgNi-BiSb-BiSb-BiSb (BCBCBCBBB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing three CuAgNi lamellae layers with each CuAgNi lamella layer deposited to a thickness of about <NUM>Å. The CuAgNi lamellae layers were modulated within the BiSbE alloy layer in the order of BiSb-CuAgNi-BiSb-BiSb-CuAgNi-BiSb-BiSb-CuAgNi-BiSb (BCBBCBBCB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing four CuAgNi lamellae layers with each CuAgNi lamella layer deposited to a thickness of about <NUM>Å. The CuAgNi lamellae layers were deposited at the bottom edge and the top edge of the BiSbE alloy layer in the order of BiSb-CuAgNi-BiSb-CuAgNi-BiSb-BiSb-CuAgNi-BiSb-CuAgNi-BiSb (BCBCBB- CBCB).

The BiSbE alloy layer of stack <NUM> was formed by depositing six BiSb lamellae layers with each BiSb lamella layer deposited to a thickness of about <NUM>Å and by depositing five CuAgNi lamellae layers with each CuAgNi lamella layer deposited to a thickness of about <NUM>Å. The CuAgNi lamellae layers were deposited throughout the BiSbE alloy layer in the order of BiSb-CuAgNi-BiSb-CuAgNi-BiSb-CuAgNi-BiSb-CuAgNi-BiSb-CuAgNi-BiSb (BCBCBCBCBCB).

Stack <NUM> with a top edge distribution of the CuAgNi, stack <NUM> with a center distribution of CuAgNi, and stack <NUM> with a modulated distribution of CuAgNi do not promote strong BiSbE (<NUM>) orientation. Stack <NUM> with a bottom edge distribution of CuAgNi, stack <NUM> with a bottom edge and top edge distribution of CuAgNi, and stack <NUM> with a CuAgNi distribution throughout the BiSbE alloy layer promoted strong BiSbE(<NUM>) orientation.

<FIG> shows a plot of the TOF-SIMS net Intensity for dopant E-Cs+ clusters across the BiSbE alloy layer for dopant elements of NiFe, Si, and CuAgNi as a function of sputter time in seconds. BiSbE sample <NUM> with atomic percent content of a dopant element of silicon of about <NUM>%, a BiSbE sample <NUM> with atomic percent content of a dopant element of CuAgNi of about <NUM>%, a BiSbE sample <NUM> with atomic percent content of a dopant element of NiFe of about <NUM>%. BiSbE sample <NUM> was formed with a modulated distribution of Si dopant element. BiSbE sample <NUM> was formed with an edge distribution of CuAgNi dopant element. BiSbE sample <NUM> was formed with an edge distribution of NiFe dopant element. The net intensity is the absolute intensity of the E-Cs+ cluster of BiSbE minus the intensity of E-Cs+ cluster of a BiSbE which contains no dopant element. Each of the samples <NUM>-<NUM> included a NiFeCu silicide seed layer of about <NUM>Å, about <NUM>Å of Cu, about <NUM>Å of NiFe, about <NUM>Å of Cu, and a NiFeCu silicide cap layer of about <NUM>Å of Cu, <NUM>Å of Si, and <NUM>Å of NiFe. The locations of the centers of the NiFeCu silicide seed layer, the NiFeCu silicide cap layer, and the BiSbE alloy layer are indicated with vertical black dashed lines.

<FIG> shows a portion of the dopant elements are pushed out of the BiSbE alloy layer. <FIG> shows a non-zero net TOF-SIMS intensity inside the BiSbE alloy layer indicating a portion of the dopant elements remain in the BiSbE lattice after deposition.

<FIG> shows TEM Cu EELS scans across a BiSbE stack comprising a silicide cap layer, a BiSbE alloy layer comprising a metallic dopant of CuAgNi, and a silicide seed layer. The BiSbE alloy layer comprised a metallic dopant of CuAgNi in an atomic percent content of about <NUM>%. The metallic dopant of CuAgNi comprised Ag in an atomic percent content of about <NUM>% and with Ni in an atomic percent content of about <NUM>%. The BiSbE stack included a NiFeCu silicide seed layer of about <NUM>Å, about <NUM>Å of Cu, a BiSbE alloy layer of about <NUM>Å, a NiFeCu silicide cap layer of about <NUM>Å, and a SiN layer of about <NUM>Å.

The BiSbE alloy layer comprised the metallic dopant element in the center of the BiSbE alloy layer going higher towards the interfaces for both room temperature and after post annealing at about <NUM> for <NUM> hours. A portion of the CuAgNi dopant element is leaving BiSb lattice and a portion of the CuAgNi dopant element is retained in the BiSb lattice even after the post annealing near the melting point of the BiSbE alloy layer.

A portion of the dopant element has been retained in the lattice after near melting. It is believed that on anneal the BiSbE lattice relaxed the lattice parameters with a portion of the dopant elements residing within the BiSbE lattice forming the alloy and with a portion diffusing to the interlayer interfaces or to the grain boundaries.

<FIG> shows the as deposited conductivity versus thickness of BiSbE alloy layers <NUM>-<NUM> comprising a metallic dopant as measured by XRR/XRF. Each of the BiSbE alloy layers <NUM>-<NUM> were formed over a Si seed layer having a thickness of about <NUM>Å. Conductivity (<NUM>/Resistance) was measured using a four-point probe. The fitted curves assume a <NUM>-resistor model of a surface conductive layer and a bulk conductive layer and fit an 'A + B/thickness' model.

BiSb layer <NUM> is a layer of pure BiSb without dopant elements, BiSbE alloy layer <NUM> comprised BiSbCu with an atomic percent content of Cu of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSbCu with an atomic percent content of Cu of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSbCu with an atomic percent content of Cu of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSb-NiFe with an atomic percent content of NiFe of about <NUM>%.

BiSbE alloy layers <NUM>, <NUM>, <NUM> showed good topological insulator properties similar to reference BiSb layer <NUM>. BiSbE alloy layer <NUM> showed bulk conduction rather than topological insulator properties.

<FIG> shows the as deposited conductivity versus thickness of various BiSbE alloy layers <NUM>-<NUM> comprising a non-metallic dopant elements of Si as measured by XRR/XRF. Each of the BiSbE alloy layers <NUM>-<NUM> were measured for thickness by XRR and were formed over a Si seed layer having a thickness of about <NUM>Å. Conductivity (<NUM>/Resistance) was measured using a four-point probe. The fitted curves assume a <NUM>-resistor model of a surface conductive layer and a bulk conductive layer and fit an 'A + B/thickness' model.

BiSb alloy layer <NUM> comprised BiSb as a reference layer. BiSbE alloy layer <NUM> comprised BiSbSi with an atomic percent content of Si of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSbSi with an atomic percent content of Si of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSbSi with an atomic percent content of Si of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSbSi with an atomic percent content of Si of about <NUM>%. BiSbE alloy layer <NUM> comprised BiSbSi with an atomic percent content of Si of about <NUM>%.

BiSbE alloy layers <NUM>-<NUM> showed good topological insulator properties similar to BiSb reference layer <NUM> after deposition. BiSbE alloys layers comprising BiSbSi having an atomic percent content of Si from <NUM>% to about <NUM>% showed good topological insulator properties.

<FIG> shows Si dopant element concentration for BiSbSi alloys vs. BiSbSi grain sizes as measured by inplane XRD patterns taken at <NUM> deg incident angle of various BiSbSi alloy layers. Each of the BiSbSi alloy layers were formed over a-Si seed layer having a thickness of about <NUM>Å and with a Si cap layer formed over the BiSbSi alloy layer having a thickness of about <NUM>Å. The BiSbSi alloy layers showed a large reduction trend in grain size as the atomic percent of Si is increased from <NUM>% to about <NUM>%. The BiSbSi alloy layers showed a small reduction trend in grain size as the atomic percent of Si is increased from more than about <NUM>%. Although the grain size of a BiSbSi alloy with an about <NUM> atomic % content of Si is much reduced in comparison to a BiSb material without dopant elements, further increasing the atomic percent content of Si above <NUM>% produces only a small additional reduction in the grain size.

<FIG> shows the surface roughness of BiSbE alloy layers <NUM>, <NUM> as determined by XRR as a function of atomic percent content of non-metallic dopant element of Si.

Each of the BiSbE alloy layers were formed over a Si seed layer having a thickness of about <NUM>Å and a Si capping layer formed thereover having a thickness of about <NUM>Å. Each of the BiSbE alloy layers were deposited to a thickness of about <NUM>Å. BiSbE alloy layer <NUM> comprised BiSbSi with varying atomic percent content of silicon. BiSbE alloy layer <NUM> comprised BiSbCu with varying atomic percent content of copper.

<FIG> shows that the dopant elements reduced interface roughness in comparison to a BiSb layer without dopant elements. The BiSbE alloy layer with an atomic percent content of the dopant element from about <NUM>% to about <NUM>% produced a large reduction in surface roughness in comparison to a BiSb material without dopant elements. The BiSbE alloy layer with an atomic percent content of the dopant element greater than <NUM>% were comparable to a BiSb material without dopant elements with larger interfacial roughness.

<FIG> shows the BiSbE alloy estimated grain size from in plane XRD patterns taken at approximately <NUM> deg. incident angle vs. estimated thickness for BiSbE by XRR for a non-metallic dopant element of Si, a metallic dopant element of Cu, a metallic dopant element of NiFe compared to BiSb without dopant elements. Estimated dopant element concentrations deposited into the film are given in the plot. BiSb layer <NUM> comprised BiSb without dopant elements. BiSbE alloy layer <NUM> comprised a dopant element Si in an atomic percent content of about <NUM>%. BiSbE alloy layer <NUM> comprised dopant element Cu in an atomic percent content of about <NUM>%. BiSbE alloy layer <NUM> comprised dopant element Cu in an atomic percent content of about Cu6% which was annealed at about <NUM> for <NUM> hours. BiSbE alloy layer <NUM> comprised dopant element NiFe in an atomic percent content of about <NUM>%. Dopant elements reduce the grain size for all BiSbE alloy thicknesses.

<FIG> is a plot of the logarithm of the intensity versus <NUM>-theta XRD out-of-the plane or coupled scans of BiSbE stacks <NUM>, <NUM>. The BiSbE alloy layer comprised a metallic dopant of CuAgNi in an atomic percent content of about <NUM>%. The metallic dopant of CuAgNi comprised Ag in an atomic percent content of about <NUM>% and with Ni in an atomic percent content of about <NUM>%. The BiSbE alloy layer was formed by depositing six BiSb lamellae layers and by depositing four CuAgNi lamellae layers. The CuAgNi lamellae layers were deposited at the bottom edge and the top edge of the BiSbE alloy layer in the order of BiSb-CuAgNi-BiSb- CuAgNi-BiSb-BiSb-CuAgNi-BiSb-CuAgNi-BiSb (BCBCBBCBCB).

Each of the stacks <NUM>, <NUM> comprised a NiFeCu-silicide layer formed to a thickness of about <NUM>Å, a copper layer formed to a thickness of about <NUM>Å, a BiSbE alloy layer formed to a thickness of about <NUM>Å, an NiFeCu-silicide layer formed to a thickness of about <NUM>Å, and a capping layer of SiN formed to a thickness of about <NUM>Å. BiSbE stack <NUM> was before annealing. BiSbE stack <NUM> is after annealing at about <NUM> for about <NUM> hours near the melting point of BiSb. BiSbE stacks <NUM>, <NUM> showed strong (<NUM>) texture before and after annealing. The BiSbE stack <NUM> showed strong (<NUM>) texture even after annealing near the melting point of BiSb with a rocking curve of about <NUM> degrees or less, such as from <NUM> degrees to <NUM> degrees. An XRR measurement of the BiSbE stack <NUM> after anneal showed a low surface roughness of about <NUM>Å or less.

Claim 1:
A spin-orbit torque, SOT, device (<NUM>), comprising:
a substrate (<NUM>); and
a bismuth antimony dopant element, BiSbE, alloy layer (<NUM>; <NUM>) over the substrate, the BiSbE
alloy layer having a (<NUM>) orientation, the BiSbE alloy layer comprising,
bismuth;
antimony; and
a dopant element,
wherein the bismuth and antimony of the BiSbE alloy layer form a plurality of BiSb lamellae layers (<NUM>),
wherein the dopant element of the BiSbE alloy layer forms one or more dopant element lamellae layers (<NUM>), each of the dopant element lamellae layers comprising a material selected from a group consisting of a non-metallic dopant element, a metallic dopant element, and combinations thereof, and
wherein the BiSbE alloy layer comprises the one or more dopant element lamellae layers at a bottom edge of the BiSbE alloy layer.