Patent Document

FIELD OF THE INVENTION 
     This invention relates to semiconductor memory devices and, more particularly, to the switching characteristics of an array of multi-layer magnetic memory cells. 
     BACKGROUND OF THE INVENTION 
     In the past, a variety of magnetic materials and structures have been utilized to form magnetoresistive materials for non-volatile memory elements, read/write heads for disk drives, and other magnetic type applications. Resistance changes due to relative changes in the magnetic states of constituent magnetic regions within these structures allow information to be stored, in the case of memories, or read, in the case of read heads. Memories made of magnetoresistive material, such as Magnetic Random Access Memory (hereinafter referred to as MRAM) has the potential to overcome some of the shortcomings associated within memories currently in production today. Dynamic Random Access Memory (DRAM), Static Random Access Memory (SRAM), and Flash are the three dominant types of memories currently in use. Each of these memory devices uses an electronic charge to store information and each has its own advantages and disadvantages. SRAM has fast read and write speeds, but it is volatile and requires large cell area. DRAM has high density, but it is also volatile and requires a refresh of the storage capacitor every few milliseconds. This requirement increases the complexity of the control electronics. FLASH is the major nonvolatile memory device in use today. FLASH uses charge trapped in a floating oxide layer to store information. Drawbacks to FLASH include high voltage requirements and slow program and erase times. Also, FLASH memory has a poor write endurance of 10 4 –10 6  cycles before memory failure. In addition, to maintain reasonable data retention, the thickness of the gate oxide has to stay above the threshold that allows electron tunneling, thus restricting FLASH&#39;s scaling trends. MRAM has the potential to have the speed performance similar to DRAM without the need for refresh, have improved density performance over SRAM without the volatility, and have improved endurance and write performance over FLASH. 
     As mentioned above magnetoresistive devices and MRAM in particular rely on resistance changes resulting from changes in the magnetization directions of constituent magnetic layers in the material stack. Typically, MRAM devices comprise a magnetic layer whose magnetization direction is fixed, the fixed layer, and a magnetic layer, the free layer, whose magnetization direction is free to switch between two or more stable directions separated by a spacer layer of an oxide (Tunneling magnetoresistance) or conductor (Giant magnetoresistance). Typical MRAM architectures involve laying out the individual magnetoresistive elements at the intersection of a crosspoint of mutually perpendicular current lines. These lines need not be in contact with the element. Their purpose is mainly to provide the magnetic fields, by having current passed along their length, to switch the magnetization direction of the free layer, within the element. In the absence of these fields, the magnetization direction of the free layer is stable. This is the procedure by which information is written to the memory. Reading information is typically accomplished by passing a small current through the element and comparing the resistance to a reference resistance. 
     For the successful operation of an MRAM device, it is required that the magnetic behavior of the free layers of an array of elements be very uniform. This is related to the crosspoint architecture mentioned above. The current lines each provide enough current to produce approximately half of the magnetic field required for the free layer to alter its state, i.e. half the switching field. Magnetic state is defined here as a stable direction of the magnetization of the free layer. The two half fields combine at the point of intersection of the current lines to provide enough field there so that the elements&#39; free layer magnetic state will change. All other bits in the array are exposed to at most approximately half the switching field. The uniformity in the magnetic behavior or the switching field for the array of bits is essential so that the half fields produced do not inadvertently cause an unwanted bit to switch its state and, in addition, that the two half fields combine to switch all the bits in the array. 
     It would be highly advantageous and is the intention of the current application, therefore, to provide means of decreasing the variation in the switching field bit to bit. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
       The foregoing and further and more specific objects and advantages of the instant invention will become readily apparent to those skilled in the art from the following detailed description of a preferred embodiment thereof taken in conjunction with the following drawings: 
         FIG. 1  is an enlarged, simplified side view of a multi-layer magnetic memory cell, in accordance with the preferred embodiment of the present invention; 
         FIG. 2  attached is a graph of the relative variation of a magnetic intrinsic anisotropy verses a thickness of a single bulk nickel iron cobalt (NiFeCo) layer; 
         FIG. 3  illustrates the relative variation of the switching field of patterned bits verses a thickness of a single patterned nickel iron cobalt (NiFeCo) layer; 
         FIG. 4  is a simplified view of a magnetic memory cell used to experimentally measure a magnetic anisotropy and a relative magnetic anisotropy variation of a magnetic layer; 
         FIG. 5  is a graph of a relative magnetic anisotropy variation of the magnetic intrinsic anisotropy illustrated in  FIG. 4  versus thickness of a magnetic layer; and 
         FIG. 6  is a graph of a relative switching variation of the magnetic memory cell illustrated in  FIG. 1  for aspect ratios of two and three versus different combinations of material stack. 
     
    
    
     DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT 
     Turn now to  FIG. 1 , which illustrates a simplified sectional view of a scalable magnetoresistive tunneling junction memory cell  10  in accordance with the present invention. The scalable magnetoresistive tunneling junction memory cell  10  includes a supporting substrate  12  onto which a seed layer  14  is positioned. Supporting substrate  12  may be, for example, a semiconductor substrate or wafer and semiconductor control devices may then be formed thereon. Seed layer  14  is formed on supporting substrate  12  to aid in the formation and operation of the remaining layers of material. An anti-ferromagnetic layer  16  is then positioned on seed layer  14  and includes, for example, alloys of manganese (Mn) and one of Ni, Fe, Pt, Rh or combinations thereof. It will be understood that seed layer  14  is optional and is included in this preferred embodiment for illustrative purposes. Also, the positioning of anti-ferromagnetic layer  16  is for fabrication convenience with many other possible configurations available. 
     A first magnetic region  18  having a resultant magnetic moment vector  20  is positioned on the anti-ferromagnetic layer  16 . A nonmagnetic separating layer  22  is placed on first magnetic region  18  and a second magnetic region  24  having a resultant magnetic moment vector  26  is positioned on nonmagnetic separating layer  22 . Nonmagnetic separating layer  22  can be a dielectric material which behaves as a tunneling barrier to produce a magnetic tunnel junction that exhibits tunneling magnetoresistance or it may be a conductive material such as copper to produce a layered metallic structure which exhibits giant magnetoresistance. It will be understood that nonmagnetic separating layer  22  can include multiple insulating layers, but is shown as one layer for illustrative purposes. 
     Anti-ferromagnetic layer  16  pins resultant magnetic moment vector  20  unidirectionally along a preferred magnetic axis unless sufficient magnetic field is supplied to overcome the pinning action of layer  16 . Generally, anti-ferromagnetic layer  16  is thick enough to insure that spurious signals and normal cell writing signals will not switch resultant magnetic moment vector  20 . 
     In the preferred embodiment, fixed magnetic region  18  includes a synthetic anti-ferromagnetic layer material which includes a tri-layer structure of an anti-ferromagnetic coupling spacer layer  28  sandwiched between a ferromagnetic layer  30  and a ferromagnetic layer  32 . However, it will be understood that magnetic region  18  can include a synthetic anti-ferromagnetic layer material other than a tri-layer structure and the use of a tri-layer structure in this embodiment is for illustrative purposes only. Further, magnetic region  18  is a fixed ferromagnetic region, meaning that the magnetic moment vectors of layers  30  and  32  are not free to rotate in the presence of a moderate applied magnetic field and layer  32  is used as the reference layer. 
     A free magnetic region  24  includes a synthetic anti-ferromagnetic layer material which includes N ferromagnetic layers that are anti-ferromagnetically coupled, wherein N is a integer number greater than or equal to two. In the embodiment shown here for simplicity, N is chosen to be equal to two so that magnetic region includes a tri-layer structure which has an anti-ferromagnetic coupling spacer layer  34  sandwiched between a ferromagnetic layer  36  and a ferromagnetic layer  38 . Ferromagnetic layers  36  and  38  each have thicknesses  40  and  42 , respectively. Further, anti-ferromagnetic coupling spacer layer  34  has a thickness  44 . It will be understood that the synthetic anti-ferromagnetic layered material in magnetic region  24  can include other structures with a different number of ferromagnetic layers and the use of a tri-layer structure in this embodiment is for illustrative purposes only. For example, a five-layer stack of a ferromagnetic layer/anti-ferromagnetic coupling spacer layer/ferromagnetic layer/anti-ferromagnetic coupling spacer layer/ferromagnetic layer could be used, wherein N is equal to three. 
     Anti-ferromagnetic coupling spacer layers  28  and  34  most often include elements Ru, Os, Re, Cr, Rh, and Cu, or combinations thereof. Further, ferromagnetic layers  30 ,  32 ,  36 , and  38  most often include alloys of Ni, Fe, Co, or combinations thereof. Ferromagnetic layers  36  and  38  each have a magnetic moment vector  46  and  48 , respectively, that are usually held anti-parallel by coupling of anti-ferromagnetic coupling spacer layer  34 . Also, magnetic region  24  has a resultant magnetic moment vector  26 . When no magnetic field is applied, resultant magnetic moment vectors  20  and  26  are oriented along a preferred anisotropy easy-axis. Further, magnetic region  24  is a free ferromagnetic region, meaning that resultant magnetic moment vector  26  is free to rotate in the presence of an applied magnetic field. 
     While anti-ferromagnetic coupling layers are illustrated between the ferromagnetic layers in magnetic regions  18  and  24 , it will be understood that the ferromagnetic layers could be anti-ferromagnetically coupled through other means such as magnetostatic fields or other features. For example, for structures with a high aspect ratio, the ferromagnetic layers are anti-parallel coupled from magnetostatic flux closure. In this case, any nonmagnetic spacer layer that breaks the ferromagnetic exchange between layers will suffice. However, in the preferred embodiment, the adjacent ferromagnetic layers are anti-ferromagnetically coupled by sandwiching anti-ferromagnetic coupling material between each adjacent ferromagnetic layer. One advantage of using a synthetic anti-ferromagnetic layer material is that the anti-parallel coupling of the magnetic moment vectors prevents a vortex from forming at a given thickness where a vortex would be formed if using a single layer. 
     Further, during fabrication of scalable magnetoresistive tunneling junction memory cell  10 , each succeeding layer (i.e.  14 ,  16 ,  30 , etc.) is deposited or otherwise formed in sequence and each cell may be defined by selective deposition, photolithography processing, etching, etc. in any of the techniques known in the semiconductor industry. During deposition of at least the ferromagnetic layers  36  and  38 , a magnetic field is provided to set an easy magnetic axis for these layers (induced anisotropy). This anisotropy axis can also be set subsequent to deposition by annealing in the presence of a magnetic field. 
     The structure of magnetic region  24  substantially impacts the variation in the switching for an array of MRAM devices. In the preferred embodiment to minimize the variation in the switching field H sw , the magnetic layer (i.e. layer  36 ) in magnetic region  24  adjacent to nonmagnetic spacer region  22  is formed to have a thickness greater than layer  38  and in the range of 40 Å to 120 Å. A thicker layer  36  has been found to significantly improve the magnetic properties of layer  36  so that H sw  is approximately equal from one MRAM device to another. In general, it has been found that the switching variation of the elements within the array is impacted by the quality of the magnetic material initially deposited on the nonmagnetic separating layer  22 . Therefore, the essence of this patent is to optimize the material quality of layer  36 , and retain acceptable switching characteristics by making layer  36  part of a SAF structure. As mentioned above SAP structures provide a reduction in the formation of magnetization vortices (where the magnetization direction is not uniaxial but circular) and a way to control the switching field See U.S. Pat. No. 6,531,723. 
     A significant degradation in the magnetic quality of magnetic layer  36  is seen starting at thicknesses below approximately 50 Å to 60 Å (See  FIG. 2 ). This can be seen by an increase in the relative variation of the intrinsic material anisotropy normalized to the mean anisotropy. Intrinsic material anisotropy is an energy defining the preferred stable uniaxial magnetization direction. The magnitude of the switching field H sw  for an unbalanced free magnetic region is controlled in part by the intrinsic anisotropy (See U.S. Pat. No. 6,531,723), and a larger variation in the intrinsic anisotropy will directly result from the increase in the variation of the magnetic switching field H sw  for patterned MRAM devices. Illustrated in  FIG. 2  is the relative variation of the intrinisic material anisotropy measured for various thicknesses  40  within a range approximately from 20 Å to 60 Å for magnetic layer  36  deposited in a magnetic field on an aluminum oxide layer  22  and annealed in a magnetic field at 250° C. for 30 minutes. As shown, the relative variation of the intrinsic anisotropy decreases for thicker magnetic layers which illustrates that magnetic memory cells grown with thicker magnetic layers positioned adjacent to the nonmagnetic spacer region will show improved magnetic properties. 
     Turn now to  FIG. 3  which illustrates a graph of the relative variation of a magnetic switching field H sw , for an array of patterned magnetic elements having a single free magnetic layer (i.e. thickness  44  equals zero and thickness  42  equals zero) verses thickness of the layer, the layer being composed of nickel iron cobalt (NiFeCo) grown on an aluminum oxide nonmagnetic spacer layer  22 . The size and shape of the elements are aspect ratio  2  ellipse shape with a width of 0.45 micrometers. As can be seen in  FIG. 3 , there is a minimum in the relative variation of the switching fields within the array beginning at approximately 40 Å. Greater than 40 Å, the relative variation is constant with thickness because it is dominated by variations in shape anisotropy from bit-to-bit that scale with the increasing moment. Below 40 Å there is an increase in the relative variation with decreasing thickness. This behavior is due to the degradation in material quality shown in  FIG. 2 . The poor magnetic properties of the thin magnetic layer directly increases the magnetic switching field variation from one MRAM device to another in the array of MRAM devices. The preferred embodiment addresses these shortcomings by making layer  36  thicker with better material quality while effectively making the whole stack thinner by anti-ferromagnetically coupling layer  38  to  36 . The preferred embodiment has the material quality of a thick layer but the shape contribution and lack of vortex formation of a thin layer. 
     Turn now to  FIG. 4  which illustrates a magnetic memory cell  50  used to experimentally measure a magnetic anisotropy and a relative magnetic anisotropy variation of SAF layers  72 . In a preferred embodiment, cell  50  includes a conductive layer  52 . An insulator layer  54  is positioned on conductive layer  52  and a magnetic layer  56  with a thickness  58  is positioned on insulator layer  54 . An anti-ferromagnetic spacer layer  60  with a thickness  62  is positioned on magnetic layer  56  and a magnetic layer  64  with a thickness  66  is positioned on spacer layer  60 . Further, an insulator layer  68  is positioned on magnetic layer  64  and a conductive layer  70  is positioned on insulator layer  68 . 
     In this specific example, conductive layers  52  and  70  include tantalum (Ta) and insulator layers  54  and  68  include aluminum oxide (AlO). Further, in this specific example, magnetic layers  56  and  64  include nickel iron (NiFe) and spacer layer  60  includes ruthenium (Ru) wherein magnetic layers  56  and  64  are anti-ferromagnetically coupled. It will be understood that the materials included in layers  52 ,  54 ,  56 ,  60 ,  64 ,  68 , and  70  of this specific example are chosen for simplicity and ease of discussion to illustrate a measurement result and that other materials could be chosen. 
     In the preferred embodiment, magnetic layers  56  and  64  are anti-ferromagnetically coupled by spacer layer  60 . However, it will be understood that magnetic layers  56  and  64  can be magnetically coupled through other means. Further, cell  50  is illustrated as including two magnetic layers (i.e. layers  56  and  64 ) for simplicity and ease of discussion to show the experimental measurement. 
     Turn now to  FIG. 5  which illustrates a graph of a relative magnetic anisotropy variation of the SAF structure  72  verses thickness  66  as illustrated in  FIG. 4 . In this illustration, thickness  66  is varied from approximately 20 Å to 120 Å wherein thickness  58  is approximately 40 Å. As shown, the relative magnetic anisotropy variation is approximately constant as a function of thickness  66 . This result indicates that the variation depends substantially on thickness  58  (See  FIG. 2 ) adjacent to tunneling barrier junction  54  and is independent of subsequent layers magnetic grown thereon (i.e. layer  64 ). 
     Turn now to  FIG. 6  which illustrates the measured improvement of the switching distribution width (sigma) of patterned bits by depositing the thick layers of an unbalanced SAF first on the tunnel barrier  22 . Shown in  FIG. 6  is a ratio of a variation for a thin magnetic layer  38  grown on a thick magnetic layer  36  divided by a variation of a thick magnetic layer  38  grown on a thin magnetic layer  36  as a function of the thin layer thickness for an array of aspect ratio  2  and  3  ellipse shaped bits of width 0.45 micrometers. For example, as thinner layer in  24  increases from 15 Å to 45 Å, the ratio of the sigmas from depositing the thick layer first on the tunnel barrier  22  to depositing the thin layer first on  22  increases from approximately 0.6 at 15 Å to 0.95 at 45 Å. The variation within an array can be reduced by as much as 40% by depositing the layer with good material quality on the tunnel barrier  22 . This result indicates that for thicknesses below approximately 50 Å the variation in the switching field for an array of elements is reduced when the thicker layer is deposited on the tunnel barrier  22 . Various changes and modifications to the embodiments herein chosen for purposes of illustration will readily occur to those skilled in the art. For example, thickness is one method for improving the material quality. In addition improved material quality can be obtained from deposition of an amorphous alloy, such as CoFeB alloys, on top of the tunnel barrier. Also material quality can be improved through high temperature anneals and depositions. To the extent that such modifications and variations do not depart from the spirit of the invention, they are intended to be included within the scope thereof which is assessed only by a fair interpretation of the following claims.

Technology Category: 5