- •Preface
- •Imaging Microscopic Features
- •Measuring the Crystal Structure
- •References
- •Contents
- •1.4 Simulating the Effects of Elastic Scattering: Monte Carlo Calculations
- •What Are the Main Features of the Beam Electron Interaction Volume?
- •How Does the Interaction Volume Change with Composition?
- •How Does the Interaction Volume Change with Incident Beam Energy?
- •How Does the Interaction Volume Change with Specimen Tilt?
- •1.5 A Range Equation To Estimate the Size of the Interaction Volume
- •References
- •2: Backscattered Electrons
- •2.1 Origin
- •2.2.1 BSE Response to Specimen Composition (η vs. Atomic Number, Z)
- •SEM Image Contrast with BSE: “Atomic Number Contrast”
- •SEM Image Contrast: “BSE Topographic Contrast—Number Effects”
- •2.2.3 Angular Distribution of Backscattering
- •Beam Incident at an Acute Angle to the Specimen Surface (Specimen Tilt > 0°)
- •SEM Image Contrast: “BSE Topographic Contrast—Trajectory Effects”
- •2.2.4 Spatial Distribution of Backscattering
- •Depth Distribution of Backscattering
- •Radial Distribution of Backscattered Electrons
- •2.3 Summary
- •References
- •3: Secondary Electrons
- •3.1 Origin
- •3.2 Energy Distribution
- •3.3 Escape Depth of Secondary Electrons
- •3.8 Spatial Characteristics of Secondary Electrons
- •References
- •4: X-Rays
- •4.1 Overview
- •4.2 Characteristic X-Rays
- •4.2.1 Origin
- •4.2.2 Fluorescence Yield
- •4.2.3 X-Ray Families
- •4.2.4 X-Ray Nomenclature
- •4.2.6 Characteristic X-Ray Intensity
- •Isolated Atoms
- •X-Ray Production in Thin Foils
- •X-Ray Intensity Emitted from Thick, Solid Specimens
- •4.3 X-Ray Continuum (bremsstrahlung)
- •4.3.1 X-Ray Continuum Intensity
- •4.3.3 Range of X-ray Production
- •4.4 X-Ray Absorption
- •4.5 X-Ray Fluorescence
- •References
- •5.1 Electron Beam Parameters
- •5.2 Electron Optical Parameters
- •5.2.1 Beam Energy
- •Landing Energy
- •5.2.2 Beam Diameter
- •5.2.3 Beam Current
- •5.2.4 Beam Current Density
- •5.2.5 Beam Convergence Angle, α
- •5.2.6 Beam Solid Angle
- •5.2.7 Electron Optical Brightness, β
- •Brightness Equation
- •5.2.8 Focus
- •Astigmatism
- •5.3 SEM Imaging Modes
- •5.3.1 High Depth-of-Field Mode
- •5.3.2 High-Current Mode
- •5.3.3 Resolution Mode
- •5.3.4 Low-Voltage Mode
- •5.4 Electron Detectors
- •5.4.1 Important Properties of BSE and SE for Detector Design and Operation
- •Abundance
- •Angular Distribution
- •Kinetic Energy Response
- •5.4.2 Detector Characteristics
- •Angular Measures for Electron Detectors
- •Elevation (Take-Off) Angle, ψ, and Azimuthal Angle, ζ
- •Solid Angle, Ω
- •Energy Response
- •Bandwidth
- •5.4.3 Common Types of Electron Detectors
- •Backscattered Electrons
- •Passive Detectors
- •Scintillation Detectors
- •Semiconductor BSE Detectors
- •5.4.4 Secondary Electron Detectors
- •Everhart–Thornley Detector
- •Through-the-Lens (TTL) Electron Detectors
- •TTL SE Detector
- •TTL BSE Detector
- •Measuring the DQE: BSE Semiconductor Detector
- •References
- •6: Image Formation
- •6.1 Image Construction by Scanning Action
- •6.2 Magnification
- •6.3 Making Dimensional Measurements With the SEM: How Big Is That Feature?
- •Using a Calibrated Structure in ImageJ-Fiji
- •6.4 Image Defects
- •6.4.1 Projection Distortion (Foreshortening)
- •6.4.2 Image Defocusing (Blurring)
- •6.5 Making Measurements on Surfaces With Arbitrary Topography: Stereomicroscopy
- •6.5.1 Qualitative Stereomicroscopy
- •Fixed beam, Specimen Position Altered
- •Fixed Specimen, Beam Incidence Angle Changed
- •6.5.2 Quantitative Stereomicroscopy
- •Measuring a Simple Vertical Displacement
- •References
- •7: SEM Image Interpretation
- •7.1 Information in SEM Images
- •7.2.2 Calculating Atomic Number Contrast
- •Establishing a Robust Light-Optical Analogy
- •Getting It Wrong: Breaking the Light-Optical Analogy of the Everhart–Thornley (Positive Bias) Detector
- •Deconstructing the SEM/E–T Image of Topography
- •SUM Mode (A + B)
- •DIFFERENCE Mode (A−B)
- •References
- •References
- •9: Image Defects
- •9.1 Charging
- •9.1.1 What Is Specimen Charging?
- •9.1.3 Techniques to Control Charging Artifacts (High Vacuum Instruments)
- •Observing Uncoated Specimens
- •Coating an Insulating Specimen for Charge Dissipation
- •Choosing the Coating for Imaging Morphology
- •9.2 Radiation Damage
- •9.3 Contamination
- •References
- •10: High Resolution Imaging
- •10.2 Instrumentation Considerations
- •10.4.1 SE Range Effects Produce Bright Edges (Isolated Edges)
- •10.4.4 Too Much of a Good Thing: The Bright Edge Effect Hinders Locating the True Position of an Edge for Critical Dimension Metrology
- •10.5.1 Beam Energy Strategies
- •Low Beam Energy Strategy
- •High Beam Energy Strategy
- •Making More SE1: Apply a Thin High-δ Metal Coating
- •Making Fewer BSEs, SE2, and SE3 by Eliminating Bulk Scattering From the Substrate
- •10.6 Factors That Hinder Achieving High Resolution
- •10.6.2 Pathological Specimen Behavior
- •Contamination
- •Instabilities
- •References
- •11: Low Beam Energy SEM
- •11.3 Selecting the Beam Energy to Control the Spatial Sampling of Imaging Signals
- •11.3.1 Low Beam Energy for High Lateral Resolution SEM
- •11.3.2 Low Beam Energy for High Depth Resolution SEM
- •11.3.3 Extremely Low Beam Energy Imaging
- •References
- •12.1.1 Stable Electron Source Operation
- •12.1.2 Maintaining Beam Integrity
- •12.1.4 Minimizing Contamination
- •12.3.1 Control of Specimen Charging
- •12.5 VPSEM Image Resolution
- •References
- •13: ImageJ and Fiji
- •13.1 The ImageJ Universe
- •13.2 Fiji
- •13.3 Plugins
- •13.4 Where to Learn More
- •References
- •14: SEM Imaging Checklist
- •14.1.1 Conducting or Semiconducting Specimens
- •14.1.2 Insulating Specimens
- •14.2 Electron Signals Available
- •14.2.1 Beam Electron Range
- •14.2.2 Backscattered Electrons
- •14.2.3 Secondary Electrons
- •14.3 Selecting the Electron Detector
- •14.3.2 Backscattered Electron Detectors
- •14.3.3 “Through-the-Lens” Detectors
- •14.4 Selecting the Beam Energy for SEM Imaging
- •14.4.4 High Resolution SEM Imaging
- •Strategy 1
- •Strategy 2
- •14.5 Selecting the Beam Current
- •14.5.1 High Resolution Imaging
- •14.5.2 Low Contrast Features Require High Beam Current and/or Long Frame Time to Establish Visibility
- •14.6 Image Presentation
- •14.6.1 “Live” Display Adjustments
- •14.6.2 Post-Collection Processing
- •14.7 Image Interpretation
- •14.7.1 Observer’s Point of View
- •14.7.3 Contrast Encoding
- •14.8.1 VPSEM Advantages
- •14.8.2 VPSEM Disadvantages
- •15: SEM Case Studies
- •15.1 Case Study: How High Is That Feature Relative to Another?
- •15.2 Revealing Shallow Surface Relief
- •16.1.2 Minor Artifacts: The Si-Escape Peak
- •16.1.3 Minor Artifacts: Coincidence Peaks
- •16.1.4 Minor Artifacts: Si Absorption Edge and Si Internal Fluorescence Peak
- •16.2 “Best Practices” for Electron-Excited EDS Operation
- •16.2.1 Operation of the EDS System
- •Choosing the EDS Time Constant (Resolution and Throughput)
- •Choosing the Solid Angle of the EDS
- •Selecting a Beam Current for an Acceptable Level of System Dead-Time
- •16.3.1 Detector Geometry
- •16.3.2 Process Time
- •16.3.3 Optimal Working Distance
- •16.3.4 Detector Orientation
- •16.3.5 Count Rate Linearity
- •16.3.6 Energy Calibration Linearity
- •16.3.7 Other Items
- •16.3.8 Setting Up a Quality Control Program
- •Using the QC Tools Within DTSA-II
- •Creating a QC Project
- •Linearity of Output Count Rate with Live-Time Dose
- •Resolution and Peak Position Stability with Count Rate
- •Solid Angle for Low X-ray Flux
- •Maximizing Throughput at Moderate Resolution
- •References
- •17: DTSA-II EDS Software
- •17.1 Getting Started With NIST DTSA-II
- •17.1.1 Motivation
- •17.1.2 Platform
- •17.1.3 Overview
- •17.1.4 Design
- •Simulation
- •Quantification
- •Experiment Design
- •Modeled Detectors (. Fig. 17.1)
- •Window Type (. Fig. 17.2)
- •The Optimal Working Distance (. Figs. 17.3 and 17.4)
- •Elevation Angle
- •Sample-to-Detector Distance
- •Detector Area
- •Crystal Thickness
- •Number of Channels, Energy Scale, and Zero Offset
- •Resolution at Mn Kα (Approximate)
- •Azimuthal Angle
- •Gold Layer, Aluminum Layer, Nickel Layer
- •Dead Layer
- •Zero Strobe Discriminator (. Figs. 17.7 and 17.8)
- •Material Editor Dialog (. Figs. 17.9, 17.10, 17.11, 17.12, 17.13, and 17.14)
- •17.2.1 Introduction
- •17.2.2 Monte Carlo Simulation
- •17.2.4 Optional Tables
- •References
- •18: Qualitative Elemental Analysis by Energy Dispersive X-Ray Spectrometry
- •18.1 Quality Assurance Issues for Qualitative Analysis: EDS Calibration
- •18.2 Principles of Qualitative EDS Analysis
- •Exciting Characteristic X-Rays
- •Fluorescence Yield
- •X-ray Absorption
- •Si Escape Peak
- •Coincidence Peaks
- •18.3 Performing Manual Qualitative Analysis
- •Beam Energy
- •Choosing the EDS Resolution (Detector Time Constant)
- •Obtaining Adequate Counts
- •18.4.1 Employ the Available Software Tools
- •18.4.3 Lower Photon Energy Region
- •18.4.5 Checking Your Work
- •18.5 A Worked Example of Manual Peak Identification
- •References
- •19.1 What Is a k-ratio?
- •19.3 Sets of k-ratios
- •19.5 The Analytical Total
- •19.6 Normalization
- •19.7.1 Oxygen by Assumed Stoichiometry
- •19.7.3 Element by Difference
- •19.8 Ways of Reporting Composition
- •19.8.1 Mass Fraction
- •19.8.2 Atomic Fraction
- •19.8.3 Stoichiometry
- •19.8.4 Oxide Fractions
- •Example Calculations
- •19.9 The Accuracy of Quantitative Electron-Excited X-ray Microanalysis
- •19.9.1 Standards-Based k-ratio Protocol
- •19.9.2 “Standardless Analysis”
- •19.10 Appendix
- •19.10.1 The Need for Matrix Corrections To Achieve Quantitative Analysis
- •19.10.2 The Physical Origin of Matrix Effects
- •19.10.3 ZAF Factors in Microanalysis
- •X-ray Generation With Depth, φ(ρz)
- •X-ray Absorption Effect, A
- •X-ray Fluorescence, F
- •References
- •20.2 Instrumentation Requirements
- •20.2.1 Choosing the EDS Parameters
- •EDS Spectrum Channel Energy Width and Spectrum Energy Span
- •EDS Time Constant (Resolution and Throughput)
- •EDS Calibration
- •EDS Solid Angle
- •20.2.2 Choosing the Beam Energy, E0
- •20.2.3 Measuring the Beam Current
- •20.2.4 Choosing the Beam Current
- •Optimizing Analysis Strategy
- •20.3.4 Ba-Ti Interference in BaTiSi3O9
- •20.4 The Need for an Iterative Qualitative and Quantitative Analysis Strategy
- •20.4.2 Analysis of a Stainless Steel
- •20.5 Is the Specimen Homogeneous?
- •20.6 Beam-Sensitive Specimens
- •20.6.1 Alkali Element Migration
- •20.6.2 Materials Subject to Mass Loss During Electron Bombardment—the Marshall-Hall Method
- •Thin Section Analysis
- •Bulk Biological and Organic Specimens
- •References
- •21: Trace Analysis by SEM/EDS
- •21.1 Limits of Detection for SEM/EDS Microanalysis
- •21.2.1 Estimating CDL from a Trace or Minor Constituent from Measuring a Known Standard
- •21.2.2 Estimating CDL After Determination of a Minor or Trace Constituent with Severe Peak Interference from a Major Constituent
- •21.3 Measurements of Trace Constituents by Electron-Excited Energy Dispersive X-ray Spectrometry
- •The Inevitable Physics of Remote Excitation Within the Specimen: Secondary Fluorescence Beyond the Electron Interaction Volume
- •Simulation of Long-Range Secondary X-ray Fluorescence
- •NIST DTSA II Simulation: Vertical Interface Between Two Regions of Different Composition in a Flat Bulk Target
- •NIST DTSA II Simulation: Cubic Particle Embedded in a Bulk Matrix
- •21.5 Summary
- •References
- •22.1.2 Low Beam Energy Analysis Range
- •22.2 Advantage of Low Beam Energy X-Ray Microanalysis
- •22.2.1 Improved Spatial Resolution
- •22.3 Challenges and Limitations of Low Beam Energy X-Ray Microanalysis
- •22.3.1 Reduced Access to Elements
- •22.3.3 At Low Beam Energy, Almost Everything Is Found To Be Layered
- •Analysis of Surface Contamination
- •References
- •23: Analysis of Specimens with Special Geometry: Irregular Bulk Objects and Particles
- •23.2.1 No Chemical Etching
- •23.3 Consequences of Attempting Analysis of Bulk Materials With Rough Surfaces
- •23.4.1 The Raw Analytical Total
- •23.4.2 The Shape of the EDS Spectrum
- •23.5 Best Practices for Analysis of Rough Bulk Samples
- •23.6 Particle Analysis
- •Particle Sample Preparation: Bulk Substrate
- •The Importance of Beam Placement
- •Overscanning
- •“Particle Mass Effect”
- •“Particle Absorption Effect”
- •The Analytical Total Reveals the Impact of Particle Effects
- •Does Overscanning Help?
- •23.6.6 Peak-to-Background (P/B) Method
- •Specimen Geometry Severely Affects the k-ratio, but Not the P/B
- •Using the P/B Correspondence
- •23.7 Summary
- •References
- •24: Compositional Mapping
- •24.2 X-Ray Spectrum Imaging
- •24.2.1 Utilizing XSI Datacubes
- •24.2.2 Derived Spectra
- •SUM Spectrum
- •MAXIMUM PIXEL Spectrum
- •24.3 Quantitative Compositional Mapping
- •24.4 Strategy for XSI Elemental Mapping Data Collection
- •24.4.1 Choosing the EDS Dead-Time
- •24.4.2 Choosing the Pixel Density
- •24.4.3 Choosing the Pixel Dwell Time
- •“Flash Mapping”
- •High Count Mapping
- •References
- •25.1 Gas Scattering Effects in the VPSEM
- •25.1.1 Why Doesn’t the EDS Collimator Exclude the Remote Skirt X-Rays?
- •25.2 What Can Be Done To Minimize gas Scattering in VPSEM?
- •25.2.2 Favorable Sample Characteristics
- •Particle Analysis
- •25.2.3 Unfavorable Sample Characteristics
- •References
- •26.1 Instrumentation
- •26.1.2 EDS Detector
- •26.1.3 Probe Current Measurement Device
- •Direct Measurement: Using a Faraday Cup and Picoammeter
- •A Faraday Cup
- •Electrically Isolated Stage
- •Indirect Measurement: Using a Calibration Spectrum
- •26.1.4 Conductive Coating
- •26.2 Sample Preparation
- •26.2.1 Standard Materials
- •26.2.2 Peak Reference Materials
- •26.3 Initial Set-Up
- •26.3.1 Calibrating the EDS Detector
- •Selecting a Pulse Process Time Constant
- •Energy Calibration
- •Quality Control
- •Sample Orientation
- •Detector Position
- •Probe Current
- •26.4 Collecting Data
- •26.4.1 Exploratory Spectrum
- •26.4.2 Experiment Optimization
- •26.4.3 Selecting Standards
- •26.4.4 Reference Spectra
- •26.4.5 Collecting Standards
- •26.4.6 Collecting Peak-Fitting References
- •26.5 Data Analysis
- •26.5.2 Quantification
- •26.6 Quality Check
- •Reference
- •27.2 Case Study: Aluminum Wire Failures in Residential Wiring
- •References
- •28: Cathodoluminescence
- •28.1 Origin
- •28.2 Measuring Cathodoluminescence
- •28.3 Applications of CL
- •28.3.1 Geology
- •Carbonado Diamond
- •Ancient Impact Zircons
- •28.3.2 Materials Science
- •Semiconductors
- •Lead-Acid Battery Plate Reactions
- •28.3.3 Organic Compounds
- •References
- •29.1.1 Single Crystals
- •29.1.2 Polycrystalline Materials
- •29.1.3 Conditions for Detecting Electron Channeling Contrast
- •Specimen Preparation
- •Instrument Conditions
- •29.2.1 Origin of EBSD Patterns
- •29.2.2 Cameras for EBSD Pattern Detection
- •29.2.3 EBSD Spatial Resolution
- •29.2.5 Steps in Typical EBSD Measurements
- •Sample Preparation for EBSD
- •Align Sample in the SEM
- •Check for EBSD Patterns
- •Adjust SEM and Select EBSD Map Parameters
- •Run the Automated Map
- •29.2.6 Display of the Acquired Data
- •29.2.7 Other Map Components
- •29.2.10 Application Example
- •Application of EBSD To Understand Meteorite Formation
- •29.2.11 Summary
- •Specimen Considerations
- •EBSD Detector
- •Selection of Candidate Crystallographic Phases
- •Microscope Operating Conditions and Pattern Optimization
- •Selection of EBSD Acquisition Parameters
- •Collect the Orientation Map
- •References
- •30.1 Introduction
- •30.2 Ion–Solid Interactions
- •30.3 Focused Ion Beam Systems
- •30.5 Preparation of Samples for SEM
- •30.5.1 Cross-Section Preparation
- •30.5.2 FIB Sample Preparation for 3D Techniques and Imaging
- •30.6 Summary
- •References
- •31: Ion Beam Microscopy
- •31.1 What Is So Useful About Ions?
- •31.2 Generating Ion Beams
- •31.3 Signal Generation in the HIM
- •31.5 Patterning with Ion Beams
- •31.7 Chemical Microanalysis with Ion Beams
- •References
- •Appendix
- •A Database of Electron–Solid Interactions
- •A Database of Electron–Solid Interactions
- •Introduction
- •Backscattered Electrons
- •Secondary Yields
- •Stopping Powers
- •X-ray Ionization Cross Sections
- •Conclusions
- •References
- •Index
- •Reference List
- •Index
\40 Chapter 4 · X-Rays
4.1\ Overview
Energetic beam electrons stimulate the atoms of the specimen to emit “characteristic” X-ray photons with sharply defined energies that are specific to each atom species. The critical condition for generating characteristic X-rays is that the energy of the beam electron must exceed the electron binding energy, the critical ionization energy Ec, for the par-
4 ticular atom species and the K-, L-, M-, and/or N- atomic shell(s). For efficient excitation, the incident beam energy should be at least twice the critical excitation energy, E0 > 2 Ec. Characteristic X-rays can be used to identify and quantify the elements present within the interaction volume. Simultaneously, beam electrons generate bremsstrahlung, or braking radiation, which creates a continuous X-ray spectrum, the “X-ray continuum,” whose energies fill the range from the practical measurement threshold of 50 eV to the incident beam energy, E0. This continuous X-ray spectrum forms a spectral background beneath the characteristic X-rays which impacts accurate measurement of the characteristic X-rays and determines a finite concentration limit of
detection. X-rays are generated throughout a large fraction of the electron interaction volume. The spatial resolution, lateral and in-depth, of electron-excited X-ray microanalysis can be roughly estimated with a modified Kanaya–Okayama range equation or much more completely described with Monte Carlo electron trajectory simulation. Because of their generation over a range of depth, X-rays must propagate through the specimen to reach the surface and are subject to photoelectric absorption which reduces the intensity at all photon energies, but particularly at low energies.
4.2\ Characteristic X-Rays
4.2.1\ Origin
The process of generating characteristic X-rays is illustrated for a carbon atom in . Fig. 4.1. In the initial ground state, the carbon atom has two electrons in the K-shell bound to the nucleus of the atom with an “ionization energy” Ec (also known as the “critical excitation energy,” the “critical
. Fig. 4.1 Schematic diagram of the process of X-ray generation: inner shell ionization by inelastic scattering of an energetic beam electron that leaves the atom in an elevated energy state which it can lower by either of two routes involving the transition of an L-shell electron to fill the K-shell vacancy: (1) the Auger process, in which the energy difference
EK – EL is transferred to another L-shell electron, which is ejected with a characteristic energy:
EK – EL – EL; (2) photon emission, in which the energy difference
EK – EL is expressed as an X-ray photon of characteristic energy
Carbon atom, |
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4.2 · Characteristic X-Rays
absorption energy,” and the “K-edge energy”) of 284 eV and four electrons in the L-shell, two each in the L1 and the L2 subshells bound to the atom, with an ionization energy of 7 eV. An incident energetic beam electron having initial kinetic energy Ein >Ec can scatter inelastically with a K-shell atomic electron and cause its ejection from the atom, providing the beam electron transfers to the atomic electron kinetic energy at least equal to the ionization energy, which is the minimum energy necessary to promote the atomic electron out of the K-shell beyond the effective influence of the positive nuclear charge. The total kinetic energy transferred to the K-shell atomic electron can range up to half the energy of the incident electron. The outgoing beam electron thus suffers energy loss corresponding to the carbon K-shell ionization energy EK =284 eV plus whatever additional kinetic energy is imparted:
Eout = Ein −EK −Ekin \ |
(4.1) |
The ionized carbon atom is left with a vacancy in the K-shell which places it in a raised energy state that can be lowered through the transition of an electron from the L-shell to fill the K-vacancy. The difference in energy between these shells must be expressed through one of two possible routes:
\1.\ The left branch in . Fig. 4.1 involves the transfer of this K–L inter-shell transition energy difference to another L-shell electron, which is then ejected from the atom with a specific kinetic energy:
Ekin = EK − EL − EL = 270eV |
\ |
(4.2a) |
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This process leaves the atom with two L-shell vacancies for subsequent vacancy-filling transitions. This ejected electron is known as an “Auger electron,” and measure-
41 |
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ment of its characteristic kinetic energy can identify the atom species of its origin, forming the physical basis for “Auger electron spectroscopy.”
\2.\ The right branch in . Fig. 4.1 involves the creation of an X-ray photon to carry off the inter-shell transition energy:
Eν = EK − EL = 277eV |
\ |
(4.2b) |
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Because the energies of the atomic shells of an element are sharply defined, the shell difference is also a sharply defined quantity, so that the resulting X-ray photon has an energy that is characteristic of the particular atom species and the shells involved and is thus designated as a “characteristic X-ray.” Characteristic X-rays are emitted uniformly in all directions over the full unit sphere with 4 π steradians solid angle. Extensive tables of characteristic X-ray energies for elements with Z≥4 (beryllium) are provided in the database embedded within the DTSAII software. The characteristic X-ray photon energy has a very narrow range of just a few electronvolts depending on atomic number, as shown in . Fig. 4.2 for the K–L3 transition.
4.2.2\ Fluorescence Yield
The Auger and X-ray branches in . Fig. 4.1 are not equally probable. For a carbon atom, characteristic X-ray emission only occurs for approximately 0.26 % of the K-shell ionizations. The fraction of the ionizations that produce photons is known as the “fluorescence yield,” ω. Most carbon K-shell ionizations thus result in Auger electron emission. The fluorescence yield is strongly dependent on the atomic number of the atom, increasing rapidly with Z, as shown in . Fig. 4.3a for K-shell ionizations. L-shell and M-shell fluorescence
. Fig. 4.2 Natural width of K-shell X-ray peaks up to 25 keV photon energy (Krause and Oliver 1979)
K-L3 Peak Width (eV, FWHM)
K-shell natural peak width vs X-ray energy
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42\ Chapter 4 · X-Rays
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yieldFluorescence |
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(photons/ionization)yield |
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0.0018 |
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0.0016 |
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0.1 |
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0.0014 |
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0.0012 |
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K-shell |
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L3-shell |
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0.0010 |
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0.01 |
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M5-shell |
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0.0008 |
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0.0006 |
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Fluorescence |
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0.0004 |
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0.0002 |
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0.0000 |
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0.0001 |
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30 |
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Atomic number |
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Atomic number, Z |
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. Fig. 4.3 a Fluorescence yield (X-rays/ionization) from the K-shell. b Fluorescence yield (X-rays/ionization) from the L3-shell. c Fluorescence yield (X-rays/ionization) from the M5-shell. d Comparison of fluorescence yields from the K-, L3- and M5- shells (Crawford et al. 2011)
yields are shown in . Fig. 4.3b, c; and K-, L-, and M-shell yields are compared in . Fig. 4.3d (Crawford et al. 2011). From . Fig. 4.3d, it can be observed that, when an element can be measured with two different shells, ωK > ωL > ωM.
The shell transitions for carbon are illustrated in the shell energy diagram shown in . Fig. 4.4a. Because of the small number of carbon atomic electrons, the shell energy values are limited, and only one characteristic X-ray energy is possible for carbon with a value of 277 eV. (The apparent possible transition from the L1-shell to the K-shell is forbidden by the quantum mechanical rules that govern these inter-shell transitions.)
4.2.3\ X-Ray Families
As the atomic number increases, the number of atomic electrons increases and the shell structure becomes more complex. For sodium, the outermost electron occupies the M-shell, so that a K-shell vacancy can be filled by a transition from the L-shell or the M-shell, producing two different characteristic X-rays, designated
″K − L2,3 ″(″Kα″) EX = EK − EL =1041eV \ |
(4.3a) |
″K − M″(″Kβ″) EX = EK − EM =1071eV \ |
(4.3b) |
For atoms with higher atomic number than sodium, additional possibilities exist for inter-shell transitions, as shown
in . Fig. 4.4b, leading to splitting of the K − L2,3 into K − L3 and K − L2 (Kα into Kα1 and Kα2), and similarly for Kβ into
Kβ1 and Kβ2, which can be observed with energy dispersive spectrometry for X-rays with energies above 20 keV.
As these additional inter-shell transitions become possible, increasingly complex “families” of characteristic X-rays are created, as shown in the energy diagrams of . Fig. 4.4c for L-shell X-rays, and 4.4d for M-shell X-rays. Only transitions that lead to X-rays that are measurable on a practical basis with energy dispersive X-ray spectrometry are shown. (There are, for example, at least 25 L-shell transitions that are possible for a heavy element such as gold, but most are of such low abundance or are so close in energy to a more abundant transition as to be undetectable by energy dispersive X-ray spectrometry.)
4.2 · Characteristic X-Rays
a
b
K-M3
Kb1 K-N3
Kb2
K-L3 K-L
Ka1 Ka22
L2
L1
K
N7 N6 N5 N4 N3 N2 N1
M5 M4 M3 M2 M1
L3
L2
L1
K
43 |
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4 |
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c |
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N7 |
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N6 |
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N5 |
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N4 |
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N3 |
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N2 |
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N1 |
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M5 |
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M4 |
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M3 |
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M2 |
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M1 |
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L3-M5 |
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L2-M4 |
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Lb1 |
L1-M3 |
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La2 |
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Lg3 |
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L2 |
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L1 |
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K |
d |
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N7 |
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N6 |
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N5 |
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N4 |
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N3 |
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N2 |
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N1 |
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M5-N7 |
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M5-N6 |
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M4-N6 |
M3-N5 |
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M4,5-N2,3 |
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Mα1 |
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Mα2 |
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Mβ |
Mγ |
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Mζ |
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M5 |
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M4 |
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M3
M2
M1
L3
L2
L1
K
. Fig. 4.4 a Atomic shell energy level diagram for carbon illustrating the permitted shell transition K–L2 (shown in green) and the forbidden transition K–L1 (shown in red). b Atomic shell energy level diagram illustrating possible K-shell vacancy-filling transitions. c Atomic shell
energy level diagram illustrating possible L-shell vacancy-filling transitions. d Atomic shell energy level diagram illustrating some possible M-shell vacancy-filling transitions
4.2.4\ X-Ray Nomenclature
Two systems are in use for designating X-rays. The traditional but now archaic Siegbahn system lists the shell where the original ionization occurs followed by a Greek letter or other symbol that suggests the order of the family members by their relative intensity, α > β > γ
> η > ζ. For closely related members, numbers are also attached, for example, Lβ1 through Lβ15. Additionally, Latin letters are used for the complex minor L-shell family members: l, s, t, u, and v. While still the predominant labeling system used in commercial X-ray microanalysis software systems, the Siegbahn system has been officially
replaced by the International Union of Pure and Applied Chemistry (IUPAC) labeling protocol in which the first term denotes the shell or subshell where the original ionization occurs while the second term indicates the subshell from which the electron transition occurs to fill the vacancy; for example, Kα1 is replaced by K-L3 for a K-shell ionization filled from the L3 subshell. . Table 4.1 gives the correspondence between the Siegbahn and IUPAC labeling schemes for the characteristic X-rays likely to be detected by energy dispersive X-ray spectrometry. Note that for the M-shell, there are minor family members detectable by EDS for which there are no Siegbahn designations.