A.C. is grateful to KoreaTech for financial support.

1. Instrumental Set-up und Kalibrierung <ol><li> Instrumental Set-up <ol><li> Verwenden Sie einen steifen diamantbeschichteten Ausleger des Typs DT-NCLR oder CDT-NCLR mit einer ersten Frequenz frei Resonanz f 0,1 ≥ 180 kHz, einen Gütefaktor Q ≥ 300 und einer Biegesteifigkeit k ≥ 40 N / m. </li><li> Montieren Sie den ausgewählten Ausleger auf einem Klemmhalter von der AFM-Herstellers. Besondere Vorsicht den Cantilever zu platzieren, so dass seine Längsachse zu der schnellen Abtastrichtung des AFM senkrecht. Alternativ kleben Sie den Ausleger auf einen Halter Ausleger von der AFM-Herstellers Zweikomponenten-Epoxid-Kleber verwendet wird. </li><li> Montieren Sie den Cantileverhalters auf die AFM Kopf und verwenden Sie den optischen Mikroskop normalerweise verfügbar mit dem AFM-System auf der AFM Cantilever zu konzentrieren. Überprüfen Sie, dass die Längsachse des Auslegers senkrecht zur Schnellscanrichtung ist. Wenn nicht, gehen Sie zurück zuAbschnitt 1.1.2. </li><li> Richten des Laserstrahls, so dass er am Ende des Auslegers reflektiert wird. Überwachen Sie die Spannungssumme an der Photodiode und führen Sie eine Feineinstellung des Summensignals zu maximieren. Typische Summensignal-Werte liegen im Bereich von 2 V. </li><li> Einstellen der horizontalen und vertikalen Neigungswinkel des Spiegels, um das reflektierte Laserfleck in der Mitte der Photodiode zu bringen, wo die Spannungen, die an die vertikale und seitliche Verschiebung entspricht nahezu Null. </li></ol></li><li> Kalibrierung <ol><li> Führen Sie einen Frequenz - Sweep die erste freie Biegeresonanz f 0,1 des Auslegers zu bestimmen. </li><li> Bestimmung der Biegesteifigkeit des Auslegers k, berechnet nach 19 (1) <img alt="Gleichung 1" src="/files/ftp_upload/54706/54706eq1.jpg" /> wobei E der Elastizitätsmodul ist, L die Länge des Auslegers, w die Breite des cantil istje, und t ist die Dicke. Dazu messen die Länge und Breite des Auslegers durch optische Mikroskopie oder Rasterelektronenmikroskopie für eine bessere Genauigkeit. Berechnen der Dicke des Auslegers aus seiner ersten Frequenz freie Biegeresonanz f 0,1, entsprechend (2) <img alt="Gleichung 2" src="/files/ftp_upload/54706/54706eq2.jpg" /> wobei ρ die Massendichte. </li><li> Wählen Sie den Standardwert der Photodiode Empfindlichkeit für den jeweiligen Auslegertyp werden für das Experiment im Setup-Menü des AFM verwendet. Bringen Sie die Cantileverspitze in Kontakt mit der Referenzprobe bei einer Last F n = 10 nN durch den Ansatz Knopf klicken. </li><li> Öffnen Sie die Kraftspektroskopie-Menü in der AFM-Software und stellen Sie die relative Ein- und Ausfahren der z-Scanner bis 50 nm und die z-Scanner Rückzug / Erweiterung auf 0,3 &amp; mgr; m / sec. Dadurch könnte die Aufzeichnung der Kraft-Weg-Kurve, die Verteiler,bestehen zunächst aus einem Zurückziehen der z-Scanner 50 nm von der Probenoberfläche entfernt und dann aus einer Reihe von Ansätzen und Einziehungen der gleichen Entfernung. </li><li> Nehmen Sie eine Kraftabstandskurve mit den eingestellten Parametern vorgeschlagen in 1.2.4 auf einer glatten und nicht-konforme Oberfläche, wie nanokristalline Diamant oder Saphir, um Probenverformungseffekte zu vermeiden. Dazu klicken Sie auf die Schaltfläche Acquire in der Kraftspektroskopie - Menü der AFM - Software. </li><li> Den abstoßend Teil der Kraft-Weg-Kurve mit einer linearen Funktion, im Kalibrierungsmenü der AFM-Software. Die inverse Steigung der Fittinglinie entspricht der Photodiode Empfindlichkeit S. Ersetzen Sie den ermittelten Wert auf den Standardwert der Gerätesoftware im Kalibrierungsmenü der AFM - Software durch die Kalibrierungstaste ausführen klicken. </li></ol></li></ol> 2. Probenvorbereitung HINWEIS: Die Probe wird in thi gemessens Experiment besteht aus einer 100 nm dicken, atomar glatten Au (111) dünnen Film auf Mica gewachsen durch physikalische Dampfabscheidung. <ol><li> Montieren Sie die Probe auf einem magnetischen Probenhalter zur Verfügung gestellt vom Hersteller des Instruments mittels eines doppelseitigen Kohlenstoffband. Um Drift der Probe während der Messungen zu vermeiden, montieren Sie die Probe einen Tag vor den Messungen, um die Kohlenstoffband entspannen zu lassen. Alternativ montieren Sie die Probe auf den Halter mit Silberfarbe, die in der Regel innerhalb von wenigen Minuten trocknet. </li><li> Montieren Sie den Magnetprobenhalter auf die x / y-Scanner. </li></ol> 3. Messverfahren <ol><li> Stellen Sie die Schwingungsfrequenz leicht off-resonance (in diesem Experiment f = 190,67 kHz) und der Schwingungsamplitude bei A = 20 nm zu beachten , dass diese Werte automatisch durch die Gerätesoftware für diese bestimmte Cantilevers eingestellt. Stellen Sie den Schwingungssollwert manuell auf einem Soll = 5 nm. </li><li> Zeichnender Ausleger in Richtung auf die Probenoberfläche den Schritt-Motor des AFM verwendet. Stellen Sie sicher, dass der Kraftsensor nicht mit der Probenoberfläche kollidiert. Halten Sie den Ausleger im Fokus während der groben Annäherung und die grobe Annäherung zu stoppen, bevor die Probenoberfläche in perfekter Bildschärfe ist. </li><li> Ansatz automatisch den Kraftsensor durch auf dem Ansatz Knopf klicken. Sobald die Schwingungsamplitude ihren Sollwert erreicht hat, ist die Spitze bereit, um die Topographie der Probenoberfläche abzutasten. </li><li> Nehmen Sie eine Reihe von Topographie Bilder auf Flächen im Bereich von 5 x 5 bis 1 x 1 um² (falls vorhanden, stellen Sie die Neigung des Topographie-Signal durch das Kippen x / y-Scanner). Stellen Sie sicher, dass aufeinanderfolgende Bilder des gleichen Bereichs zeigen keine Zeichen von Drift und dass die z-Scannerposition bleibt nahezu konstant. Ist dies nicht der Fall ist, weiterhin Abbildungs ​​bis das System stabilisiert hat. </li><li> Sobald sich das System stabilisiert hat und eine glatte 1 x 1 um² Bereich gefunden wurde, ziehen sich die force Sensor wenige Mikrometer von der Oberfläche der Probe auf der Rückzugs - Taste anklicken. </li><li> Wählen Sie die Kraftspektroskopie-Modus im Gerätemenü und bewegen Sie den Kraftsensor auf der Mitte des vorgewählten 1 x 1 um² Bereich, mit einer Kraft-Sollwert von 10 nm. Überwachen der Position des z-Abtaster, bis sie konstant bleibt. </li><li> Wählen Sie die 2 x 2 Punktraster, dessen Mittelpunkt entspricht dem Zentrum der vorgewählten 1 x 1 um² Fläche. Die Entfernung zwischen zwei benachbarten Punkten nächsten bei 500 nm. </li><li> Stellen Sie den relativen Abstand scanner 0-150 nm zu variieren bei einer Geschwindigkeit von 300 nm / sec und dann zurückziehen über den gleichen Abstand und mit der gleichen Geschwindigkeit. Gegeben gelten den Neigungswinkel des Auslegers in Bezug auf die Probenoberfläche, eine Neigungskorrektur durch den seitlichen Scanner durch Z × tan φ Bewegen während eines vertikalen Scanners Verlängerungs Z, wobei φ der Neigungswinkel 20. HINWEIS: Ein paar instruments Konto für den Ausleger Neigung in ihrer Kraftspektroskopie oder Einrückungsmodus; dies ist der Fall für die AFM in dieser Arbeit verwendet. </li><li> Drücken Sie die Start-Taste in der Gerätesoftware den Erwerb der AFM Einzug von Daten zu beginnen. </li><li> Sobald die AFM Indentationsmessungen abgeschlossen haben, fahren Sie das Kraftsensor wenige Mikrometer von der Probenoberfläche entfernt. </li><li> Wählen Sie den berührungslosen AFM-Modus-Bildgebung in der Gerätesoftware-Menü und wiederholen Sie den beschriebenen Verfahren in den Abschnitten 3.1 und 3.2. </li><li> Führen Sie einen Scan über den gleichen 1 x 1 um² Oberfläche, wie in Abschnitt 3.3, um die genaue Position der Einzüge zu lokalisieren. Weitere Oberflächenscans über einen 500 x 500 nm² Oberfläche kann die verbleibenden Einzüge mit näher Bild durchgeführt werden. </li></ol> 4. Datenanalyse <ol><li> Bildverarbeitung <ol><li> Verarbeiten Sie die aufgezeichneten Bilder Topographie, um die Linien in der Schnellscan dir ausrichtenEIL basierend auf mittlere Differenz. Verwenden Sie die integrierte Funktion von Gwyddion. </li></ol></li><li> Berechnen Sie die projizierte Fläche A p von Einrückungen die Vertiefung Analysefunktion von Gwyddion verwenden. </li><li> Schätzen Sie die AFM - Spitze Form der Topographiebilder von Einrückungen durch die Spitze Analysefunktion von Gwyddion verwenden. Dann Mittelwert der Spitzenform Bilder und messen Sie die Halböffnungswinkel α der gemittelten Spitzenform. </li><li> Konvertieren Sie die Kraft-Weg - Kurven in Kraft- Weg -Kurven , die durch die Spitze Verschiebung Berechnung δ gemäß 13 (3) <img alt="Gleichung 3" src="/files/ftp_upload/54706/54706eq3.jpg" /> wobei Z die relative Scannerposition. </li><li> Nun zeichnen Sie die Kraft gegenüber der Spitze Verschiebung. Die resultierende Kurve zeigt in der Regel so genannte Pop-Ins, mit Längen im Bereich von mehreren 100 pm, die auf atomistischen Plastizität Ereignisse entsprechen. Verwenden Sie die erste von these Pop-Ins die Spitze Verschiebung an der Elastizitätsgrenze δ el 4 zu bestimmen. </li><li> Den elastischen Teil der Kraft- Weg -Kurve mit der Hertzian Funktion 21. (4) <img alt="Gleichung 4" src="/files/ftp_upload/54706/54706eq4.jpg" /> wobei R der Spitzenradius und E &#39;* der reduzierte Elastizitätsmodul, gegeben durch <img alt="Gleichung 5" src="/files/ftp_upload/54706/54706eq5.jpg" /> Mit M s, t die Einbuchtung Modul der Probe und der Spitze ist, respectively. In diesem Fall ist die Fitparameter <img alt="Gleichung 6" src="/files/ftp_upload/54706/54706eq6.jpg" /> . </li><li> Verlängern Sie die Anpassungsfunktion in die Plastizität Regime , um die Arbeit der Plastizität W Plastizität von der Flächendifferenz zwischen der Anpassungsfunktion und der experimentellen Kurve 21 zu berechnen. </li><li> Berechne die Härte der Probe nach 1, 2 (5) <img alt="Gleichung 7" src="/files/ftp_upload/54706/54706eq7.jpg" /> und (6) <img alt="Gleichung 8" src="/files/ftp_upload/54706/54706eq8.jpg" /> wobei F n, die maximale max Last angelegt ist, ist A p die projizierte Fläche des in Abschnitt berechnet Gedankenstrich 4.2, α der halbe Öffnungswinkel der Spitze in Abschnitt 4.3, δ el ist die Spitze Verschiebung bei der ersten Plastizität berechnet ist Ereignis und δ max ist die maximale Spitze Verschiebung (siehe Abschnitt 4.4). </li></ol>

<ol>
	<li>Tabor, D. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> The hardness of metals. , (1951).</li><li>Fischer-Cripps, A. C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Nanoindentation. , (2004).</li><li>Michalke, T. A., Houston, J. E. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Dislocation+Nucleation+at+Nano-Scale+Mechanical+Contacts.">Dislocation Nucleation at Nano-Scale Mechanical Contacts.</a> Acta Mater. 46 (2), 391-396 (1998).</li><li>Kiely, J. D., Houston, J. E. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanomechanical+Properties+of+Au(111)+(001),+and+(110)+Surfaces.">Nanomechanical Properties of Au(111) (001), and (110) Surfaces.</a> Phys. Rev. B. 57 (19), 12588 (1998).</li><li>Kiely, J. D., Jarausch, K. F., Houston, J. E., Russell, P. E. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Initial+Stages+of+Yield+in+Nanoindentation.">Initial Stages of Yield in Nanoindentation.</a> J. Mater. Res. 14 (19), 2219-2227 (1999).</li><li>Egberts, P., Bennewitz, R. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Atomic+Scale+Nanoindentation:+Detection+and+Indentification+of+Single+Glide+Events+in+Three+Dimensions+by+Force+Microscopy.">Atomic Scale Nanoindentation: Detection and Indentification of Single Glide Events in Three Dimensions by Force Microscopy.</a> Nanotechnology. 22 (42), 425703-1-425703-9 (2011).</li><li>Filleter, T., Bennewitz, R. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanometer+Scale+Plasticity+of+Cu(100).">Nanometer Scale Plasticity of Cu(100).</a> Nanotechnology. 18 (4), 044004-1-044004-4 (2007).</li><li>Asenjo, A., Jaafar, M., Carrasco, E., Rojo, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Dislocation+mechanisms+in+the+first+stage+of+plasticity+of+nanoindented+Au(111)+surfaces.">Dislocation mechanisms in the first stage of plasticity of nanoindented Au(111) surfaces.</a> Phys. Rev. B. 73 (7), 075431 (2006).</li><li>Paul, W., Oliver, D., Miyahara, Y., Gruetter, P. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Minimum+threshold+for+incipient+plasticity+in+the+atomic-scale+nanoindentation+of+Au(111).">Minimum threshold for incipient plasticity in the atomic-scale nanoindentation of Au(111).</a> Phys. Rev. Lett. 110 (13), 135506 (2013).</li><li>Kracke, B., Damaschke, B. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Measurement+of+nanohardness+and+nanoelasticity+of+thin+gold+films+with+scanning+force+microscope.">Measurement of nanohardness and nanoelasticity of thin gold films with scanning force microscope.</a> Appl. Phys. Lett. 77 (3), 361-363 (2000).</li><li>Sansoz, F., Gang, T. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=A+force-mapping+method+for+quantitative+hardness+measurements+by+atomic+force+microscopy+with+diamond-tipped+sapphire+cantilevers.">A force-mapping method for quantitative hardness measurements by atomic force microscopy with diamond-tipped sapphire cantilevers.</a> Ultramicroscopy. 111, 11-19 (2010).</li><li>Silva, E. C. C. M., Van Vliet, K. J. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Robust+approach+to+maximize+the+range+and+accuracy+of+force+application+in+atomic+force+microscopes+with+non-linear+position-sensitive+detectors.">Robust approach to maximize the range and accuracy of force application in atomic force microscopes with non-linear position-sensitive detectors.</a> Nanotechnolgy. 17 (21), 5525-5529 (2006).</li><li>Caron, A., Bennewitz, R. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Lower+Nanometer-Scale+Size+Limit+for+the+Deformation+of+a+Metallic+Glass+by+Shear+Transformations+Revealed+by+Quantitative+AFM+Indentation.">Lower Nanometer-Scale Size Limit for the Deformation of a Metallic Glass by Shear Transformations Revealed by Quantitative AFM Indentation.</a> Beilstein J. Nanotechnol. 6, 1721-1732 (2015).</li><li>Andriotis, O. G., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanomechanical+assesment+of+human+and+murine+collagen+fibrils+via+atomic+force+microscopy+cantilever-based+nanoindentation.">Nanomechanical assesment of human and murine collagen fibrils via atomic force microscopy cantilever-based nanoindentation.</a> J. Mech. Behavior Biomed. Mater. 39, 9-26 (2014).</li><li>Bischel, M. S., Vanlandingham, M. R., Eduljee, R. F., Gillespie, J. W., Schultz, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=On+the+use+of+nanoscale+indentation+with+the+AFM+in+the+identification+of+phases+in+blends+of+linear+low+density+polyethylene+and+high+density+polyethylene.">On the use of nanoscale indentation with the AFM in the identification of phases in blends of linear low density polyethylene and high density polyethylene.</a> J. Mater. Sci. 35 (1), 221-228 (2000).</li><li>Zhang, L., Wang, W., Zheng, L., Wang, X., Yan, Q. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Quantitative+characterization+of+mechanical+property+of+annealed+monolayer+colloidal+crystal.">Quantitative characterization of mechanical property of annealed monolayer colloidal crystal.</a> Langmuir. 32 (2), 451-459 (2016).</li><li>Ne&#269;as, D., Klapetek, P. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Gwyddion:+An+open-source+software+for+SPM+data+analysis.">Gwyddion: An open-source software for SPM data analysis.</a> Cent. Eur. J. Phys. 10 (1), 181-188 (2012).</li><li>Hahn, B. H., Valentine, D. T. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Essential Matlab for Engineers and Scientists. , (2013).</li><li>Nonnenmacher, M., Greschner, J., Wolter, O., Kassing, R. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Scanning+Force+Microscopy+with+Micromachined+Silicon+Sensors.">Scanning Force Microscopy with Micromachined Silicon Sensors.</a> J. Vac. Sci. Technol. B. 9 (2), 1358-1362 (1991).</li><li>Cannara, R. J., Brukman, M. J., Carpick, R. W. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Cantilever+tilt+compensation+for+variable-load+atomic+force+microscopy.">Cantilever tilt compensation for variable-load atomic force microscopy.</a> Rev. Sci. Instrum. 76 (5), 053706 (2005).</li><li>Johnson, K. L. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Contact Mechanics. , (1985).</li><li>Mohr, M., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Young's+Modulus,+Fracture+Strength,+and+Poisson's+Ratio+of+Nanocrystalline+Diamond+Films.">Young's Modulus, Fracture Strength, and Poisson's Ratio of Nanocrystalline Diamond Films.</a> J. Appl. Phys. 116 (12), 124308-1-124308-10 (2014).</li><li>Arnault, J. C., Mosser, A., Zamfirescu, M., Pelletier, H. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Elastic+recovery+measurements+performed+by+atomic+force+microscopy+and+standard+nanoindentation+on+a+Co(10.1)+monocrystal.">Elastic recovery measurements performed by atomic force microscopy and standard nanoindentation on a Co(10.1) monocrystal.</a> J. Mater. Res. 17 (6), 1258-1265 (2002).</li><li>Cao, Y., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanoindentation+measurements+of+the+mechanical+properties+of+polycrystalline+Au+and+Ag+thin+films+on+silicon+substrates:+Effect+of+grain+size+and+film+thickness.">Nanoindentation measurements of the mechanical properties of polycrystalline Au and Ag thin films on silicon substrates: Effect of grain size and film thickness.</a> Mater. Sci. Eng. A. 457 (1-2), 232-240 (2006).</li><li>Lilleodden, E. T., Nix, W. D. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Microstructural+length-scale+effects+in+the+nanoindentation+behavior+of+thin+gold+films.">Microstructural length-scale effects in the nanoindentation behavior of thin gold films.</a> Acta Mater. 54 (6), 1583-1593 (2006).</li><li>Corcoran, S. G., Colton, R. J., Lilleodden, E. T., Gerberich, W. W. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Anomalous+plastic+deformation+at+surfaces:+Nanoindentation+of+gold+single+crystals.">Anomalous plastic deformation at surfaces: Nanoindentation of gold single crystals.</a> Phys. Rev. B. 55 (24), R16057 (1997).</li><li>Van Vliet, K. J., Li, J., Zhu, T., Yip, S., Suresh, S. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Quantifying+the+early+stages+of+plasticity+through+nanoscale+experiments+and+simulations.">Quantifying the early stages of plasticity through nanoscale experiments and simulations.</a> Phy. Rev. B. 67 (10), 104105 (2003).</li></ol>

The authors have nothing to disclose.

Es wurde ein Verfahren zum Durchführen einer Reihe von Vertiefungen auf einer Au (111) Dünnfilmoberfläche mit einem Diamantbeschichtetes AFM-Spitze dargestellt. Berührungslos AFM-Bildgebung und AFM Vertiefung wurden mit dem gleichen Kraftsensor ausgeführt. Die Anforderungen für die berührungslose Bildgebung eine hohe erste freie Resonanzfrequenz f 0,1 ≥ 180 kHz und einem hohen Qualitätsfaktor Q ≥ 300. In AFM Vertiefung sind, die vertikale Kraft im Bereich von mehreren Mikronewton...

For the last 150 years, hardness values have been used to characterize the mechanical behavior of materials and to predict their performance under various loading conditions. The hardness of a material describes the resistance of its surface to the penetration of a harder indenter. For metallic materials, the hardness relates to resistance to plastic flow.
Although the implementation of hardness testing has proven to be relatively easy, the yielded results have long been rather empirical, making them unable to describe the intrinsic properties of the investigated material. The empirical nature of hardness testing results has been a consequence of the use of various indenter geometries, each of which has a different established hardness scale. However, all empirical hardness scales, such as the Brinell hardness (HB) test for spherical indenters and the Vickers (HV) and Knoop (HK) hardness tests for different types of four-sided pyramids, have one thing in common: the hardness number is determined from the ratio of the applied load to the developed area of the remaining indent. In an attempt to relate the hardness of metals to their fundamental mechanical properties, the hardness measured with a spherical indenter has been defined as the ratio of the applied load to the projected area of the remaining indent. This hardness value, also known as the Meyer's hardness (H), is equal to the mean contact pressure and directly relates to the yield strength of non-work-hardening metals1. 
Hardness testing has long been limited to the macro-scale, in which case the sizes of indents have been measured by optical means. The development of instrumented indentation, where force-displacement curves are recorded, has been recognized as a valuable alternative for determining the hardness of a material, although the size of the remaining indent may be too small to be accurately imaged. In this case, the projected area of the indent is calculated from the tip displacement according to a so-called indenter-area function2. Due to this development, the analysis of the curvature of force-displacement curves and of the occurrence of distinct plasticity events in the shape of pop-ins is now widely used to study the mechanisms of plastic deformation at the micrometer scale, such as by means of nanoindentation3.
It is well accepted that the carriers of plastic deformation in metals, i.e., dislocations, operate at the nanometer scale. To understand their modes of operation at the atomic level, new experimental techniques with atomic resolution are needed. Initial investigations of atomistic plasticity events at the interfaces between nanometer-sized single asperities and single crystalline Au surfaces of different orientations have been carried out by interfacial force microscopy (IFM)4, 5. Atomic force microscopy (AFM) indentation has been applied to observe the nucleation and gliding of single dislocations in KBr(100) single crystals6, Cu(100)7, and Au(111)8, 9. There, atomistic plasticity events were observed in the shape of pop-ins, with lengths in the range of 1 &#197;. AFM indentation has also been used to measure the nano-hardness and -elasticity of gold nano-island grown on mica10. In this work, the nano-hardness was found to be smaller than the bulk value and was observed to depend linearly on the indentation area. Also, a detailed measurement protocol has been proposed to determine the hardness of hard surfaces, such as fused quartz and silicon, by AFM indentation with a diamond-tipped sapphire cantilever11. In particular, this method takes into account the non-linearity of the photo-sensitive deflection detectors for large cantilever deflection12. More recently, AFM indentation and non-contact AFM imaging have been combined to quantitatively determine the hardness and the fundamental mechanisms of plastic deformation of a Pt(111) single crystalline surface and Pt-based metallic glass13. For Pt(111), plastic deformation mechanisms at the nanometer scale were found to be consistent with the discrete mechanisms established for larger scales. Further, the nanometer-scale plastic deformation of the metallic glass was found to be not discrete, but rather continuous and highly localized around the indenting tip. These results revealed a lower size limit for metallic glasses, below which shear transformation mechanisms are not activated by indentation. AFM indentation has also been used to determine the hardness values of biological samples (such as collagen fibrils)14, polymers15, and colloidal crystals16.
In the present work, a careful experimental procedure is described that includes the force sensor selection, its calibration, the calibration of the cantilever deflection detection system, and the minimization of instrumental drift for accurate and reproducible force-distance measurements. Also, a method for the data analysis is presented that allows the extraction of force-penetration curves from recorded force-distance curves. Further representative results are shown and discussed in the light of recent findings in the field of plastic deformation of small volumes.
For this experiment, an atomic force microscope (AFM) was used. The cornerstone of an AFM is its micro-fabricated force sensor (usually a cantilever beam), with a sharp tip at the end whose radius is in the range of several nanometers. In the particular configuration of the instrument used for this experiment, the cantilever is mounted onto a piezo-electric z-scanner, while the sample to be investigated is mounted onto a piezo-electric x/y-scanner. During AFM imaging, the force sensor tip is scanned over a sample to register interaction forces with the sample surface that result in a deflection of the cantilever according to Hooke's law. The static or dynamic deflection of the cantilever can be measured with an optical beam deflection detector, consisting of a laser diode, a set of mirrors, and a photodiode that converts the cantilever deflection into a voltage. During imaging, the signal at the photodiode is controlled by a feedback loop so as to keep the interaction forces at the sample surface; this results in adjustments of the z-scanner position, which are recorded and displayed as a topography image.
Prerequisites for the experiment described below are that the piezo-electric scanners of the atomic force microscope are well-calibrated and that the instrument stays in the laboratory at a constant temperature and humidity level. The reader should be aware that, depending on the atomic force microscope model, some of the experimental procedure steps may have to be modified. In particular, all measurements are performed after setting the scanners' ranges to "small"; this function allows for the reduction of the x/y-scanner range to 5 x 5 &#181;m&#178; and the z-scanner range to 4 &#181;m, which ensures a resolution at small scales. This function is not available on all commercial AFM and is not mentioned in the remainder of the text.
For data analysis, the use of the free SPM data analysis software Gwyddion17 and the Matlab software package18 are recommended.
This protocol gives a description of the experimental procedure to be followed in order to perform instrumented hardness measurements by AFM. Since the handling of different commercial AFMs may differ from one model to the other, the reader should refer to the manual provided by the AFM manufacturer for detailed setting procedures and software information. In the following text, in order to reproduce the described experiment, it is assumed that the reader is familiar with the handling of the particular AFM used here.

<table><tbody><tr><td>AFM XE-100</td><td>Park Instruments</td><td>discontinued</td><td>Atomic force microscope</td></tr><tr><td>CDT-NCLR</td><td>NanoSensors</td><td>CDT-NCLR</td><td>Conductive diamond coated non-contact lever</td></tr><tr><td>100 nm thick Au(111) thin film on Mica</td><td>Phasis</td><td>20020011</td><td>atomically smooth gold thin film</td></tr></tbody></table>

quantitative hardness measurement by instrumented afm-indentation

In this work, a combination of amplitude-modulated non-contact atomic force microscopy and atomic force spectroscopy is applied for instrumented hardness measurements on an Au(111) surface with atomistic resolution of single plasticity events. A careful experimental procedure is described that includes the force sensor selection, its calibration, the calibration of the cantilever deflection detection system, and the minimization of instrumental drift for accurate and reproducible force-distance measurements. Also, a method for the data analysis is presented that allows the extraction of force-penetration curves from recorded force-distance curves. A typical curve displays a clear elastic deformation regime up to the first plasticity event, or pop-in, with a length in the range of one to two Burger's vectors. Later plasticity events exhibit the same magnitude. The work of plasticity is further extracted from the measurements. Finally, the hardness is determined in combination with the indentation curve using non-contact atomic force microscopy images of the remaining indents.

In dieser Arbeit wurde die Biegesteifigkeit des Auslegers k berechnet sich nach der geometrischen Balkentheorie 19. Für die spezielle diamantbeschichteten Ausleger in dieser Arbeit verwendeten, fanden wir k = 55,69 N / m. Beachten Sie, dass wir die Diamantbeschichtung vernachlässigt; die Dicke der Diamantschicht beträgt ein bis zwei Größenordnungen kleiner als der Auslegerdicke und damit nicht signifikant seine Biegesteifigkeit nicht erhöht (obwohl sein...

Watch this Scientific Journal Video about Quantitative Hardness Measurement by Instrumented AFM-indentation at JoVE.com

Quantitative Hardness Measurement by Instrumented AFM-indentation

This experimental protocol describes how atomic force microscopy can be used to measure hardness at the true nanometer scale and to detect single atomistic plasticity events.

Quantitative Härtemessung durch Instrumented AFM-Einzug

In this work, a combination of amplitude-modulated non-contact atomic force microscopy and atomic force spectroscopy is applied for instrumented hardness ...

quantitative-hardness-measurement-by-instrumented-afm-indentation

Research

JoVE Journal

Engineering

9.6K Aufrufe.  KoreaTech, Korea University of Technology and Education. This experimental protocol describes how atomic force microscopy can be used to measure hardness at the true nanometer scale and to detect single atomistic plasticity events. 

Serie: Quantitative Hardness Measurement by Instrumented AFM-indentation

Measuring the Mechanical Properties of Living Cells Using Atomic Force Microscopy

Mechanical properties of cells and extracellular matrix (ECM) play important roles in many biological processes including stem cell differentiation, tumor formation, and wound healing. Changes in stiffness of cells and ECM are often signs of changes in cell physiology or diseases in tissues. Hence, cell stiffness is an index to evaluate the status of cell cultures. Among the multitude of methods applied to measure the stiffness of cells and tissues, micro-indentation using an Atomic Force Microscope (AFM) provides a way to reliably measure the stiffness of living cells. This method has been widely applied to characterize the micro-scale stiffness for a variety of materials ranging from metal surfaces to soft biological tissues and cells. The basic principle of this method is to indent a cell with an AFM tip of selected geometry and measure the applied force from the bending of the AFM cantilever. Fitting the force-indentation curve to the Hertz model for the corresponding tip geometry can give quantitative measurements of material stiffness. This paper demonstrates the procedure to characterize the stiffness of living cells using AFM. Key steps including the process of AFM calibration, force-curve acquisition, and data analysis using a MATLAB routine are demonstrated. Limitations of this method are also discussed.

This paper demonstrates a protocol to characterize the mechanical properties of living cells by means of microindentation using an Atomic Force Microscope (AFM).

Messung der mechanischen Eigenschaften von lebenden Zellen mit Atomic Force Microscopy

Mechanical  properties of cells and extracellular matrix (ECM) play important roles in many  biological processes including stem cell differentiation, ...

Forschung

Biotechnik

Characterization Of Multi-layered Fish Scales (Atractosteus spatula) Using Nanoindentation, X-ray CT, FTIR, and SEM

The hierarchical architecture of protective biological materials such as mineralized fish scales, gastropod shells, ram&#8217;s horn, antlers, and turtle shells provides unique design principles with potentials for guiding the design of protective materials and systems in the future. Understanding the structure-property relationships for these material systems at the microscale and nanoscale where failure initiates is essential. Currently, experimental techniques such as nanoindentation, X-ray CT, and SEM provide researchers with a way to correlate the mechanical behavior with hierarchical microstructures of these material systems1-6. However, a well-defined standard procedure for specimen preparation of mineralized biomaterials is not currently available. In this study, the methods for probing spatially correlated chemical, structural, and mechanical properties of the multilayered scale of A. spatula using nanoindentation, FTIR, SEM, with energy-dispersive X-ray (EDX) microanalysis, and X-ray CT are presented.

Characterization Of Multi-layered Fish Scales Atractosteus spatula Using Nanoindentation, X-ray CT, FTIR, and SEM

This paper presents the methods used for probing spatially correlated chemical, structural, and mechanical properties of the multilayered scale of Atractosteus spatula (A. spatula) using nanoindentation, Fourier transform infrared (FTIR) spectroscopy, scanning electron microscopy (SEM), and X-ray computed tomography (X-ray CT). The experimental results have been used to investigate the design principles of protective biological materials.

Charakterisierung von mehrschichtigen Fischschuppen (<em&gt; Atractosteus Spachtel</em&gt;) Verwendung Nanoindentierung, Röntgen-CT-, FTIR-und SEM

The hierarchical architecture of protective biological materials such as mineralized fish scales, gastropod shells, ram&#8217;s horn, antlers, and turtle ...

Use of Atomic Force Microscopy to Measure Mechanical Properties and Turgor Pressure of Plant Cells and Plant Tissues

We present here the use of atomic force microscopy to indent plant tissues and recover its mechanical properties. Using two different microscopes in indentation mode, we show how to measure an elastic modulus and use it to evaluate cell wall mechanical properties. In addition, we also explain how to evaluate turgor pressure. The main advantages of atomic force microscopy are that it is non-invasive, relatively rapid (5~20 min), and that virtually any type of living plant tissue that is superficially flat can be analyzed without the need for treatment. The resolution can be very good, depending on the tip size and on the number of measurements per unit area. One limitation of this method is that it only gives direct access to the superficial cell layer.

Here, we present atomic force microscopy (AFM), operated as a nano- and micro-indentation tool on cells and tissues. The instrument allows the simultaneous acquisition of 3D surface topography of the sample and its mechanical properties, including cell wall Young's modulus as well as turgor pressure.

Einsatz der Atomkraftmikroskopie zur Messung mechanischer Eigenschaften und Turgordruck von Pflanzenzellen und Pflanzengeweben

We present here the use of atomic force microscopy to indent plant tissues and recover its mechanical properties. Using two different microscopes in ...

Entwicklungsbiologie

Covalent Attachment of Single Molecules for AFM-based Force Spectroscopy

Atomic force microscopy (AFM)-based single molecule force spectroscopy is an ideal tool for investigating the interactions between a single polymer and surfaces. For a true single molecule experiment, covalent attachment of the probe molecule is essential because only then can hundreds of force-extension traces with one and the same single molecule be obtained. Many traces are in turn necessary to prove that a single molecule alone is probed. Additionally, passivation is crucial for preventing unwanted interactions between the single probe molecule and the AFM cantilever tip as well as between the AFM cantilever tip and the underlying surface. The functionalization protocol presented here is reliable and can easily be applied to a variety of polymers. Characteristic single molecule events (i.e., stretches and plateaus) are detected in the force-extension traces. From these events, physical parameters such as stretching force, desorption force and desorption length can be obtained. This is particularly important for the precise investigation of stimuli-responsive systems at the single molecule level. As exemplary systems poly(ethylene glycol) (PEG), poly(N-isopropylacrylamide) (PNiPAM) and polystyrene (PS) are stretched and desorbed from SiOx (for PEG and PNiPAM) and from hydrophobic self-assembled monolayer surfaces (for PS) in aqueous environment.

Covalent attachment of probe molecules to atomic force microscopy (AFM) cantilever tips is an essential technique for the investigation of their physical properties. This allows us to determine the stretching force, desorption force and length of polymers via AFM-based single molecule force spectroscopy with high reproducibility.

Kovalente Befestigung einzelner Moleküle für die AFM-basierte Kraftspektroskopie

Atomic force microscopy (AFM)-based single molecule force spectroscopy is an ideal tool for investigating the interactions between a single polymer and ...

Chemie

Atomic Force Microscopy Cantilever-Based Nanoindentation: Mechanical Property Measurements at the Nanoscale in Air and Fluid

An atomic force microscope (AFM) fundamentally measures the interaction between a nanoscale AFM probe tip and the sample surface. If the force applied by the probe tip and its contact area with the sample can be quantified, it is possible to determine the nanoscale mechanical properties (e.g., elastic or Young&#39;s modulus) of the surface being probed. A detailed procedure for performing quantitative AFM cantilever-based nanoindentation experiments is provided here, with representative examples of how the technique can be applied to determine the elastic moduli of a wide variety of sample types, ranging from kPa to GPa. These include live mesenchymal stem cells (MSCs) and nuclei in physiological buffer, resin-embedded dehydrated loblolly pine cross-sections, and Bakken shales of varying composition.
Additionally, AFM cantilever-based nanoindentation is used to probe the rupture strength (i.e., breakthrough force) of phospholipid bilayers. Important practical considerations such as method choice and development, probe selection and calibration, region of interest identification, sample heterogeneity, feature size and aspect ratio, tip wear, surface roughness, and data analysis and measurement statistics are discussed to aid proper implementation of the technique. Finally, co-localization of AFM-derived nanomechanical maps with electron microscopy techniques that provide additional information regarding elemental composition is demonstrated.

Quantifying the contact area and force applied by an atomic force microscope (AFM) probe tip to a sample surface enables nanoscale mechanical property determination. Best practices to implement AFM cantilever-based nanoindentation in air or fluid on soft and hard samples to measure elastic modulus or other nanomechanical properties are discussed.

Rasterkraftmikroskopie Cantilever-basierte Nanoindentation: Messungen mechanischer Eigenschaften auf der Nanoskala in Luft und Flüssigkeit

An atomic force microscope (AFM) fundamentally measures the interaction between a nanoscale AFM probe tip and the sample surface. If the force applied by ...

Ingenieurwesen

Characterizing Multiscale Mechanical Properties of Brain Tissue Using Atomic Force Microscopy, Impact Indentation, and Rheometry

To design and engineer materials inspired by the properties of the brain, whether for mechanical simulants or for tissue regeneration studies, the brain tissue itself must be well characterized at various length and time scales. Like many biological tissues, brain tissue exhibits a complex, hierarchical structure. However, in contrast to most other tissues, brain is of very low mechanical stiffness, with Young&#39;s elastic moduli E on the order of 100s of Pa. This low stiffness can present challenges to experimental characterization of key mechanical properties. Here, we demonstrate several mechanical characterization techniques that have been adapted to measure the elastic and viscoelastic properties of hydrated, compliant biological materials such as brain tissue, at different length scales and loading rates. At the microscale, we conduct creep-compliance and force relaxation experiments using atomic force microscope-enabled indentation. At the mesoscale, we perform impact indentation experiments using a pendulum-based instrumented indenter. At the macroscale, we conduct parallel plate rheometry to quantify the frequency dependent shear elastic moduli. We also discuss the challenges and limitations associated with each method. Together these techniques enable an in-depth mechanical characterization of brain tissue that can be used to better understand the structure of brain and to engineer bio-inspired materials.

We present a set of techniques to characterize the viscoelastic mechanical properties of brain at the micro-, meso-, and macro-scales.

Charakterisieren Multiskalige Mechanische Eigenschaften von Gehirngewebe mittels Rasterkraftmikroskopie, Schlag Einrückungen und Rheometrie

To design and engineer materials inspired by the properties of the brain, whether for mechanical simulants or for tissue regeneration studies, the brain ...

Neurowissenschaften

Micro-Mechanical Characterization of Lung Tissue Using Atomic Force Microscopy

Matrix stiffness strongly influences growth, differentiation and function of adherent cells1-3. On the macro scale the stiffness of tissues and organs within the human body span several orders of magnitude4. Much less is known about how stiffness varies spatially within tissues, and what the scope and spatial scale of stiffness changes are in disease processes that result in tissue remodeling. To better understand how changes in matrix stiffness contribute to cellular physiology in health and disease, measurements of tissue stiffness obtained at a spatial scale relevant to resident cells are needed. This is particularly true for the lung, a highly compliant and elastic tissue in which matrix remodeling is a prominent feature in diseases such as asthma, emphysema, hypertension and fibrosis. To characterize the local mechanical environment of lung parenchyma at a spatial scale relevant to resident cells, we have developed methods to directly measure the local elastic properties of fresh murine lung tissue using atomic force microscopy (AFM) microindentation. With appropriate choice of AFM indentor, cantilever, and indentation depth, these methods allow measurements of local tissue shear modulus in parallel with phase contrast and fluorescence imaging of the region of interest. Systematic sampling of tissue strips provides maps of tissue mechanical properties that reveal local spatial variations in shear modulus. Correlations between mechanical properties and underlying anatomical and pathological features illustrate how stiffness varies with matrix deposition in fibrosis. These methods can be extended to other soft tissues and disease processes to reveal how local tissue mechanical properties vary across space and disease progression.

The stiffness of the extracellular matrix strongly influences multiple behaviors of adherent cells. Matrix stiffness varies spatially throughout a tissue, and undergoes modification in various disease conditions. Here we develop methods to characterize spatial variations in stiffness in normal and fibrotic mouse lung tissue using atomic force microscopy microindentation.

Micro-Mechanische Charakterisierung von Lungengewebe mit Atomic Force Microscopy

Matrix stiffness strongly influences growth, differentiation and function of adherent cells1-3.  On the macro scale the stiffness of tissues and organs ...

Biologie

Application of Atomic Force Microscopy to Detect Early Osteoarthritis

Biomechanical properties of cells and tissues not only regulate their shape and function but are also crucial for maintaining their vitality. Changes in elasticity can propagate or trigger the onset of major diseases like cancer or osteoarthritis (OA). Atomic force microscopy (AFM) has emerged as a strong tool to qualitatively and quantitatively characterize the biomechanical properties of specific biological target structures on a microscopic scale, measuring forces in a range from as small as the piconewton to the micronewton. Biomechanical properties are of special importance in musculoskeletal tissues, which are subjected to high levels of strain. OA as a degenerative disease of the cartilage results in the disruption of the pericellular matrix (PCM) and the spatial rearrangement of the chondrocytes embedded in their extracellular matrix (ECM). Disruption in PCM and ECM has been associated with changes in the biomechanical properties of cartilage. In the present study we used AFM to quantify these changes in relation to the specific spatial pattern changes of the chondrocytes. With each pattern change, significant changes in elasticity were observed for both the PCM and ECM. Measuring the local elasticity thus allows for drawing direct conclusions about the degree of local tissue degeneration in OA.

We present a method to investigate early osteoarthritic changes at the cellular level in articular cartilage by using atomic force microscopy (AFM).

Anwendung der Atomkraftmikroskopie zur Erkennung früher Osteoarthritis

Biomechanical properties of cells and tissues not only regulate their shape and function but are also crucial for maintaining their vitality. Changes in ...

Experimental and Data Analysis Workflow for Soft Matter Nanoindentation

Nanoindentation refers to a class of experimental techniques where a micrometric force probe is used to quantify the local mechanical properties of soft biomaterials and cells. This approach has gained a central role in the fields of mechanobiology, biomaterials design&#160;and tissue engineering, to obtain a proper mechanical characterization of soft materials with a resolution comparable to the size of single cells (&#956;m). The most popular strategy to acquire such experimental data is to employ an atomic force microscope (AFM); while this instrument offers an unprecedented resolution in force (down to pN) and space (sub-nm), its usability is often limited by its complexity that prevents routine measurements of integral indicators of mechanical properties, such as Young&#39;s Modulus (E). A new generation of nanoindenters, such as those based on optical fiber sensing technology, has recently gained popularity for its ease of integration while allowing to apply sub-nN forces with &#181;m spatial resolution, therefore being suitable to probe local mechanical properties of hydrogels and cells.
In this protocol, a step-by-step guide detailing the experimental procedure to acquire nanoindentation data on hydrogels and cells using a commercially available ferrule-top optical fiber sensing nanoindenter is presented. Whereas some steps are specific to the instrument used herein, the proposed protocol can be taken as a guide for other nanoindentation devices, granted some steps are adapted according to the manufacturer&#39;s guidelines. Further, a new open-source Python software equipped with a user-friendly graphical user interface for the analysis of nanoindentation data is presented, which allows for screening of incorrectly acquired curves, data filtering, computation of the contact point through different numerical procedures, the conventional computation of E, as well as a more advanced analysis particularly suited for single-cell nanoindentation data.

The protocol presents a complete workflow for soft material nanoindentation experiments, including hydrogels and cells. First, the experimental steps to acquire force spectroscopy data are detailed; then, the analysis of such data is detailed through a newly developed open-source Python software, which is free to download from GitHub.

Experimenteller und Datenanalyse-Workflow für die Nanoindentation weicher Materie

Nanoindentation refers to a class of experimental techniques where a micrometric force probe is used to quantify the local mechanical properties of soft ...

Addressing Practical Issues in Atomic Force Microscopy-Based Micro-Indentation on Human Articular Cartilage Explants

Without a doubt, atomic force microscopy (AFM) is currently one of the most powerful and useful techniques to assess micro and even nano-cues in the biological field. However, as with any other microscopic approach, methodological challenges can arise. In particular, the characteristics of the sample, sample preparation, type of instrument, and indentation probe can lead to unwanted artifacts. In this protocol, we exemplify these emerging issues on healthy as well as osteoarthritic articular cartilage explants. To this end, we first show via a step-by-step approach how to generate, grade, and visually classify ex vivo articular cartilage discs according to different stages of degeneration by means of large 2D mosaic fluorescence imaging of the whole tissue explants. The major strength of the ex vivo model is that it comprises aged, native, human cartilage that allows the investigation of osteoarthritis-related changes from early onset to progression. In addition, common pitfalls in tissue preparation, as well as the actual AFM procedure together with the subsequent data analysis, are also presented. We show how basic but crucial steps such as sample preparation and processing, topographic sample characteristics caused by advanced degeneration, and sample-tip interaction can impact data acquisition. We also subject to scrutiny the most common problems in AFM and describe, where possible, how to overcome them. Knowledge of these limitations is of the utmost importance for correct data acquisition, interpretation, and, ultimately, the embedding of findings into a broad scientific context.

We present a step-by-step approach to identify and address the most common problems associated with atomic force microscopy micro-indentations. We exemplify the emerging problems on native human articular cartilage explants characterized by various degrees of osteoarthritis-driven degeneration.

Auseinandersetzung mit praktischen Fragen der Rasterkraftmikroskopie-basierten Mikroeindringung an menschlichen Gelenkknorpelexplantaten

Without a doubt, atomic force microscopy (AFM) is currently one of the most powerful and useful techniques to assess micro and even nano-cues in the ...