Classifications

• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B15/00—Single-crystal growth by pulling from a melt, e.g. Czochralski method
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B13/00—Single-crystal growth by zone-melting; Refining by zone-melting
  • C30B13/08—Single-crystal growth by zone-melting; Refining by zone-melting adding crystallising materials or reactants forming it in situ to the molten zone
  • C30B13/10—Single-crystal growth by zone-melting; Refining by zone-melting adding crystallising materials or reactants forming it in situ to the molten zone with addition of doping materials
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
  • C30B11/04—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method adding crystallising materials or reactants forming it in situ to the melt
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
  • C30B11/04—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method adding crystallising materials or reactants forming it in situ to the melt
  • C30B11/08—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method adding crystallising materials or reactants forming it in situ to the melt every component of the crystal composition being added during the crystallisation
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B13/00—Single-crystal growth by zone-melting; Refining by zone-melting
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B13/00—Single-crystal growth by zone-melting; Refining by zone-melting
  • C30B13/08—Single-crystal growth by zone-melting; Refining by zone-melting adding crystallising materials or reactants forming it in situ to the molten zone
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B15/00—Single-crystal growth by pulling from a melt, e.g. Czochralski method
  • C30B15/02—Single-crystal growth by pulling from a melt, e.g. Czochralski method adding crystallising materials or reactants forming it in situ to the melt
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B15/00—Single-crystal growth by pulling from a melt, e.g. Czochralski method
  • C30B15/02—Single-crystal growth by pulling from a melt, e.g. Czochralski method adding crystallising materials or reactants forming it in situ to the melt
  • C30B15/04—Single-crystal growth by pulling from a melt, e.g. Czochralski method adding crystallising materials or reactants forming it in situ to the melt adding doping materials, e.g. for n-p-junction
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
  • C30B29/02—Elements
  • C30B29/06—Silicon
• • C—CHEMISTRY; METALLURGY
  • C30—CRYSTAL GROWTH
  • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
  • C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
  • C30B29/10—Inorganic compounds or compositions
  • C30B29/52—Alloys
• • H—ELECTRICITY
  • H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
  • H10F—INORGANIC SEMICONDUCTOR DEVICES SENSITIVE TO INFRARED RADIATION, LIGHT, ELECTROMAGNETIC RADIATION OF SHORTER WAVELENGTH OR CORPUSCULAR RADIATION
  • H10F71/00—Manufacture or treatment of devices covered by this subclass
  • H10F71/121—The active layers comprising only Group IV materials
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
  • Y02E10/00—Energy generation through renewable energy sources
  • Y02E10/50—Photovoltaic [PV] energy
  • Y02E10/547—Monocrystalline silicon PV cells
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
  • Y02P70/50—Manufacturing or production processes characterised by the final manufactured product

Definitions

• the present disclosure relates to methods and systems for use in the fabrication of semiconductor materials such as silicon, for example using lower- grade silicon. More particularly, the present disclosure relates to a method and system for forming a silicon crystal or ingot with improved mechanical and electrical characteristics, using feedstock material of various grades and germanium enrichment.
• Materials alternatives for the bulk of current solar cells range from mono-crystalline silicon wafers, for example based on very clean raw silicon such as electronic-grade (EG) silicon feedstock needed for the IC industry, to multi-crystalline (mc) silicon wafers based on not as clean raw silicon such as the so-called solar-grade (SOG) silicon feedstock or an even lower-quality material called upgraded metallurgical-grade ( UMG) silicon feedstock.
• EG electronic-grade
• mc multi-crystalline
• SOG solar-grade
• UMG upgraded metallurgical-grade
• Low-grade feedstock materials for the PV industry such as UMG silicon
• UMG silicon are typically processed into ingots and wafers of mc-silicon where the ultimate, solar cell relevant quality is typically controlled by grain boundaries, other structural defects and a relatively high concentration of impurities such as transition metals.
• impurities such as transition metals.
• carbon related and oxygen related defects in the wafer bulk can degrade cell properties, in particular when associated with metals, Some species of the broad defect spectrum may be passivated with hydrogen to reduce their electrical degradation potential.
• CZ Czochralski
• FZ Floating Zone
• Wafer breakage is initiated by crack formation and subsequent propagation. Cracks may originate from, for example, handling-induced local damage on surfaces, in particular at edges and corners. State-of-the-art solar ceil manufacturing technology uses careful handling and processing of wafers and solar cells to avoid such situations. Intrinsic material strength of bulk silicon is also a function of bulk lattice defects. Of particular concern are defects that generate local tensile lattice strain, enabling internal crack
• Such a process should be easily transferable to higher-grade, non-UMG feedstock silicon which is used partially or exclusively for producing mono-crystalline silicon materials, for example by applying the CZ technique or the FZ technique.
• a technique is here disclosed for the crystallization of silicon which may be useful for ultimately making solar cells.
• the present disclosure includes a method and system for making silicon ingots or crystals with improved electrical and mechanical material characteristics, for use in a variety of solar cell applications.
• a silicon ingot forming method and associated system are provided for using a low-grade silicon feedstock that includes forming within a crucible device a molten solution from a low-grade silicon feedstock and a predetermined amount of germanium. The process and system perform a directional solidification of the molten solution to form a silicon ingot within the crucible
• a silicon ingot forming method and associated system are provided for adding not only a predetermined amount of germanium but also a predetermined amount of Ga to a silicon feedstock of various grades.
• a silicon crystal forming method and associated system are provided for using a higher-grade silicon feedstock and a predetermined amount of germanium. The process and system perform a crystallization of the molten solution to form a silicon crystal.
• crystallization is achieved using the CZ technique, where a predetermined amount of germanium is added to the higher-grade silicon feedstock before meltdown and subsequent CZ crystal pulling.
• crystallization is achieved using the FZ technique, where the predetermined amount of germanium is attached to the high-grade silicon supply rod before applying the floating melt zone for FZ crystal growing.
• the predetermined amount of germanium can be added in pure form. It can be also part of a compound such as a pure silicon-germanium alloy.
• FIG . I is a prior art general process for the formation of a solar cell beginning with the formation of a silicon ingot
• FIG. 2 illustrates conceptually a process flow for producing a silicon ingot with improved characteristics according to the present disclosure:
• FIG . 3 provides a process flow for one embodiment the present disclosure employing low-grade raw silicon feedstock for a directional solidification ingot formation process
• FIG. 4 provides a process flow for one embodiment of the present disclosure employing higher-grade raw silicon feedstock for a CZ crystal pulling process
• FIG. 5 provides a process flow for one embodiment the present disclosure employ ing a supply rod of high-grade raw silicon feedstock for an FZ crystal growing process
• FIG. 6 illustrates conceptually another process flow for producing a silicon ingot with improved characteristics according to the present disclosure
• FIG. 7 shows a diagram of breakage test results on a plurality of different wafers tested from a reference ingot and an engineered ingot using an embodiment of the present disclosure
• FIG . 8 illustrates a diagram of breakdown voltage test results on a plurality of different wafers tested from a reference ingot and an engineered ingot using an embodiment of the present disclosure.
• the method and system of the present disclosure provide a
• FIG. 1 depicts a known process 10 beginning at step 12.
• MG or other low-grade silicon enters known wafer forming process flow 10
• Known process flow 10 extracts high-grade silicon from MG silicon at step 14.
• High-grade silicon extraction step 14 is a high-cost processing sequence resulting in EG silicon or somewhat relaxed silicon quality called SOG feedstock quality.
• SOG feedstock quality Those are the types of silicon feedstock materials used for making the ingot in step 16.
• Known process flow 10 includes slicing the silicon ingot, generally using a wire-saw to derive a silicon wafer at step 18. The resulting silicon wafers then enter solar ceil formation process 20 using the resulting wafer.
• FIG . 2 depicts, in general terms, novel aspects of how the disclosed process may be integrated into the overall solar cell fabrication flow 30.
• the improved silicon ingot characteristics arising from the present disclosure may include greater mechanical strength , and better electrical characteristics such as recombination lifetime of the resulting wafers, and hence the resulting solar cells, using feedstock material of various grades and the presently disclosed germanium enrichment steps.
• Fabrication flow 30 includes using MG silicon at step 32 that may be purified to some degree to become UMG silicon. The resulting silicon quality still results in low-grade silicon 34. Accordingly, silicon quality 34 relates to much lower cost as compared to silicon quality 14. Also, low-grade silicon ingot 34 includes a higher content of metallic and non metallic impurities as compared to silicon quality 14. The present disclosure includes the addition or
• silicon ingot formation may occur using, for example, a directional solidification process, a CZ crystal formation process, or a FZ crystal formation process. Adjustment of the cry stallization conditions based on actually applied germanium concentrations further enhances mechanical properties and electrical properties.
• Step 40 represents the formation of silicon wafers.
• the solar cell forming process occurs at step 42.
• FIG . 3 provides a process flo w 50 for one embodiment of the present disclosure employing low-grade raw silicon feedstock.
• a first step 52 includes placing low-grade raw silicon (e.g., UMG silicon) into a crucible. Before the heating process for silicon melt formation begins, the present disclosure contemplates the addition, at step 54, of a predetermined amount of pure germanium (e.g., germanium with a purity of 99.99 percent or 99.999 percent) to the low-grade silicon feedstock.
• a predetermined amount of pure germanium e.g., germanium with a purity of 99.99 percent or 99.999 percent
• the total range of added germanium in impro ved silicon may range from 5 to 200 ppmw.
• Another embodiment may allow for a range of germanium from 5 to 50 ppmw.
• Another embodiment may allow for a range of germanium from 20 to 40 ppmw.
• Another embodiment may allow for a range of germanium from 30 to 40 ppmw.
• Another embodiment may allow for a range of germanium from 50 to 100 ppmw.
• Another embodiment may allow for a range of germanium from 50 to 200 ppmw.
• Another embodiment may allow for a range of germanium from 100 to 150 ppmw. .
• Another embodiment may allow for a range of germanium from 120 to 180 ppmw.
• step 56 includes heating the solid mixture for generating a melt of the low-grade silicon and added germanium at step 58,
• the molten low- grade silicon and germanium may be subsequently crystallized, step 60, by performing a directional solidification, for example.
• FIG. 4 provides a process flow 70 for a further embodiment of the present disclosure employing higher-grade raw silicon feedstock.
• a first step 72 includes placing higher-grade raw silicon (e.g., EG silicon) into a crucible.
• higher-grade raw silicon e.g., EG silicon
• the present disclosure contemplates the addition, at step 74 of a predetermined amount of pure germanium (e.g., germanium with a purity at least of 99,999) to the higher-grade silicon feedstock.
• step 76 includes heating the solid mixture for generating a melt of the higher-grade silicon and added germanium, step 78.
• a portion of molten higher-grade silicon and germanium may be subsequently formed into a silicon crystal, step 80, by pulling a CZ crystal using established procedures for achieving and maintaining desired crystal properties throughout the CZ process.
• FIG. 5 provides a process flow 90 for a further embodiment the present disclosure starting with a supply rod of high-grade raw silicon, specifically EG silicon feedstock.
• a first step 92 includes beginning with a high-grade raw silicon (e.g., EG silicon) supply rod.
• the supply rod allows the use of a floating zone or FZ region for an FZ crystallization process.
• the present disclosure contemplates the addition, at step 94, of a predetermined amount of pure germanium (e.g., germanium with a purity at least of 99.999) to the supply rod of high-grade raw silicon feedstock.
• step 96 includes using the floating melt zone of the higher-grade silicon and added germanium, step 98, to subsequently form a silicon crystal, step 100, by growing an FZ crystal from the supply rod and germanium mixture.
• FIG. 6 depicts, in general terms, novel aspects of another process that may be integrated into the overall solar cell fabrication flow 130.
• Fabrication flow 130 includes using MG silicon at step 132 that may be purified to some degree to become UMG silicon.
• the resulting silicon quality still results in low- grade silicon 134.
• silicon quality 134 relates to much lower cost as compared to unmodified silicon as described in Figure 1.
• low-grade silicon ingot 134 includes a higher content of metallic and non metallic impurities as compared to unmodified silicon.
• the present disclosure includes adding germanium in conjunction with further addition or enhancement of a
• gallium 136 for the purpose of further improving properties, including mechanical and electrical properties of the resulting ingot.
• gallium is added at concentrations in a range of 0 to 10 ppniw.
• the combina tion of silicon with germanium and gallium are heated to form a silicon melt as an initial aspect of ingot formation step 138.
• FIG. 7 depicts a characteristic result 110 of an experiment comparing the mechanical wafer strength of an example of germanium-doped material from ingot B with non-doped reference material from ingot A.
• the very same type of UMG feedstock silicon has been selected, and the casting was done sequentially with the same tool applying the same casting conditions.
• an d one set of near-top wafers were selected for determining the mechanical wafer strength, measured as ratio of maximum external force F n -, ax over maximum wafer deformation l rnax in a standard 4-line bending test.
• the normalized wafer strength (strength divided by wafer thickness) 112 is presented for the various wafer groups where the sequence number 114 describes the original location within respective ingots (increasing numbers from bottom to top). From the graph we see that wafers from the germanium-doped ingot B exhibit higher strength than wafers from the reference ingot A. The results shown here support the conclusion that the addition of germanium in the formation of a silicon ingot yield greater strength characteristics than a silicon ingot made from an otherwise identically formed silicon ingot.
• the Table reports data for a medium-grade feedstock that was used in formation of a multi-crystalline silicon ingot. The above data shows
• the improved material characteristics of a silicon ingot formed consistent with the teachings of the present disclosure ha ve a cascading effect to promote a corresponding reduction in the final costs associated with the manufacture of solar cells and systems using such solar cells. That is, because the germanium doped silicon material exhibits improved material strength and flexibility over non-doped silicon material, a greater likelihood exists that the mechanical processes of slicing the wafers from the ingot will result in less wafer breakage. Then, once the wafers are sliced, the continuing material strength and flexibility of the silicon wafers provide increased durability as such silicon wafers are further formed into solar cells.
• Such resulting solar cells are less likely to break, crack, or demonstrate fracture stress upon installation or shipping from the solar cell manufacturing site to the points of assembly as solar cell arrays and the final installation in the field of such solar cell arrays.
• the increased durability and flexibility of such solar cells may further increase the operational life of the solar cell arrays, as weathering, thermal and environmental transients in the field may damage or otherwise occur.
• the germanium-doping example may cause an increase in not only the carrier lifetime of respecti ve silicon material but also the overall solar cell efficiency. This is seen, for example, in the demonstrated increase in recombination lifetime of 20.7% and a measured cell efficiency increase of 1.2% in the above Table.
• Figure 8 further illustrates further improvements in electrical properties of the silicon material as a result of an addition of germanium as described in the present disclosure.
• the Figure shows breakdown voltage versus a wafer identification number, where a lower wafer identification number indicates a location near a bottom of an ingot, and a higher wafer identification number indicates a location near a top of an ingot.
• the reference ingot data 150 shows consistently lower breakdown voltages than ingots processed according to embodiments of the invention 152.
• an effective amount of germanium for addition to the silicon depends on a number of potentially competing factors. For example although mechanical properties such as strength and flexibility can be enhanced by adding more germanium, additions over a certain concentration can introduce unwanted effects such as formation of silicon carbides. Therefore, for example, concentrations of germanium in the range of 5 to 50 ppmw provide enhanced electrical properties such as low light-induced degradation and high recombination lifetimes, along with enhanced mechanical strength and low dislocation densities, while keeping unwanted effects to a minimum.
• an effective amount of germanium includes concentrations of germanium in the range of 0 to 20 ppmw. In one example, an effective amount of germanium includes concentrations of germanium in the range of 30 to 60 ppmw.
• the silicon material improvements of the present disclosure may derive from increased compressive lattice strain associated with substitutionally incorporating germanium atoms in the lattice structure of crystalline silicon, Such substitutional incorporation of germanium may compensate local tensile stresses associated with certain bulk defects in silicon wafers or solar cells and result in impro ved control of the intrinsic material strength.
• Empirical results indicate that a silicon material with germanium in sufficient amounts demonstrates an increased material strength. The best practical range depends on the material quality generated. Slightly higher germanium concentrations turn out to work better for mono-crystalline silicon, as compared to multi-crystalline silicon.
• the disclosed subject matter provides a method and system for forming a silicon ingot or crystal which includes forming within a crucible device a molten solution from silicon feedstock and a predetermined amount of germanium, followed by either directional solidification to form an ingot within the crucible, pulling CZ crystals from the melt, or growing FZ crystals.

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• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Inorganic Chemistry (AREA)
• Crystals, And After-Treatments Of Crystals (AREA)
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• Photovoltaic Devices (AREA)

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• 2010
  • 2010-11-24 US US12/954,498 patent/US8758507B2/en not_active Expired - Fee Related
• 2011
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