WO2012115944A1 - Procédé de fabrication d'une lame et lame de qualité chirurgicale en verre métallique massif - Google Patents

Procédé de fabrication d'une lame et lame de qualité chirurgicale en verre métallique massif Download PDF

Info

Publication number
WO2012115944A1
WO2012115944A1 PCT/US2012/025903 US2012025903W WO2012115944A1 WO 2012115944 A1 WO2012115944 A1 WO 2012115944A1 US 2012025903 W US2012025903 W US 2012025903W WO 2012115944 A1 WO2012115944 A1 WO 2012115944A1
Authority
WO
WIPO (PCT)
Prior art keywords
blade
metallic glass
bulk metallic
edge
deformation
Prior art date
Application number
PCT/US2012/025903
Other languages
English (en)
Inventor
Alex J. KREJCIE
Shiv G. KAPOOR
Ann HERDENDORF
Richard E. Devor
Original Assignee
The Board Of Trustees Of The University Of Illinois
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by The Board Of Trustees Of The University Of Illinois filed Critical The Board Of Trustees Of The University Of Illinois
Publication of WO2012115944A1 publication Critical patent/WO2012115944A1/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/11—Making amorphous alloys

Definitions

  • a field of the invention is blade fabrication and surgical grade blades.
  • Example applications of the invention include fabrication of high quality surgical blades, e.g., for ophthalmological surgery, or other blades having very small cutting edge radii.
  • Diamond has been the preferred material of choice among surgeons for knife blades used in precisions surgeries such as ophthalmic surgeries.
  • Single crystal diamond provides extreme hardness and sharpness. These blades are expensive though, and cause a typical ophthalmic surgical knife to be about $2000-3000. See, C.H. Williamson, "Diamond knives: Are They a Clear Choice for Clear Corneal Cataract Surgery?,” Cataract and Refractive Surgery Today, June 2007, 82-84.
  • the diamond knife blade edges are also somewhat fragile, and require careful handling to maintain the integrity of the cutting edge.
  • the diamond knifed blades are also difficult to manufacture. While natural diamond is itself expensive, difficulty in manufacturing the blade cutting edge geometries, particularly the edge radius, plays a role in the expense of the diamond blade instruments. While alternative processes and materials are available, achieving high performance at a low cost is still a problem.
  • Typical techniques for manufacturing the diamond knife cutting edge geometry include mechanical lapping, thermo-chemical lapping, chemically-assisted mechanical polishing and planarization (CAMPP) and reactive ion etching. See, I. Miyamoto, K. Kawata, M. Kimura, N.
  • Kanekama "Sharpening diamond knives having a small apex angle of less than 55° with high-energy argon ion beams," Journal of Materials Science Letters, 1988; 7(11): 1175-1177; W. J. Zong, D. Li, K. Cheng, T. Sun, H.X. Wang, Y.C. Liang, "The material removal mechanism in mechanical lapping of diamond cutting tools," International Journal of Machine Tools and Manufacture, 2005; 45(7-8): 783-788; W. J. Zong, D. Li, K. Cheng, T. Sun, Y.C.
  • Stainless steel yields a much larger edge radius than diamond blades (-300 nm) due to the limitation of its crystalline structure. This results in poorer cutting performance and longer heal times. Additionally, stainless steel lacks durability to sustain its cutting edge over multiple uses.
  • J. Albanese, G. Dugue, V. Parvu, A.M. Bajart, E. Lee "Evaluation of a new disposable silicon limbal relaxing incision knife by experienced users," BMC Ophthalmology, 2009; 9:15. However, like stainless steel, they do not perform well over multiple incisions.
  • Peker et al. U.S. Patent No, 6,887,586 discloses a process for forming cutting tools, including surgical blades, from bulk amorphous alloys. This process relies upon a separate sharpening step that uses conventional sharpening, such as lapping, chemical machining and high energy methods. Careful handling is required for these separate sharpening steps to maintain the integrity of the edge, and reliable manufacturing of very small edge radiuses is likely difficult and expensive.
  • An embodiment of the invention is a fabrication process for making a blade.
  • the process heats bulk metallic glass to a supercooled state. While in the supercooled stated, a blade is shaped in the bulk metallic glass. The blade is then drawn to deform the blade and form a surgical grade edge on the blade.
  • the process can provide a surgical grade blade consisting of bulk metallic glass shaped as a blade and having an edge with a radius of -lOOnm or less. In preferred embodiments, the edge has a radius of ⁇ 5nm-100nm. The blade edge transitions from the localized necked material to the very small edge radius produced from drawing, providing a robust surgical grade blade.
  • FIGs. 1A-1G are schematic cross-sectional views illustrating a preferred embodiment process for fabricating a bulk metallic glass surgical grade blade of the invention
  • FIG. 2 is a schematic diagram of a micromolding system that can be used to fabricate bulk metallic glass surgical grade blades
  • FIGs. 3-5 show the load cell force data from multiple fabrication tests at three different temperatures (650K, 660K, 670K) for demonstrating the method of FIGs. 1A-1G;
  • FIGs. 6A-6P are SEM images of a blade and blade edges formed during experiments
  • FIG. 7 shows a plot of temperature versus feedrate for all tests with the results qualitatively assessed to be either good or poor
  • FIG. 8A illustrates different deformation modes as a function of strain rate and temperature for the bulk metallic glass Zr 41 . 25 Tin .75 Cu ) 2. 5 Ni i oBe 2 2.5, which was used in experiments to form blade edges;
  • FIG. 8 B illustrates peak force versus feed rate for temperatures of 650K, 660K and 670K; and
  • FIG. 8C illustrates drawing distance versus federate at the three different temperatures;
  • FIG. 9 illustrates the type of deformation occurring for 660K and 100 ⁇ /s as a function of force and drawing distance
  • FIGs. 10A-10D are example images from the video of the 660 K and 100 ⁇ /s test at selected drawing distances that were used to obtain the data in FIG. 9;
  • FIG. 11 illustrates the type of deformation occurring for 660K and 1000 ⁇ /s as a function of force and drawing distance
  • FIGs. 12A-12D are example images from the video of the 660 K and 1000 ⁇ /s test at selected drawing distances that were used to obtain the data in FIG. 1 1;
  • FIG. 13 illustrates the type of deformation occurring for 670K and 750 ⁇ /s as a function of feree and drawing distance
  • FIGs. 14A-14E are example images from the video of the 670 K and 750 ⁇ /s test at selected drawing distances that were used to obtain the data in FIG. 13;
  • FIGs. 15A-15D show a selection of various edges formed under different temperatures and with different deformation rates (670K, 500 ⁇ /8; 650 , 500 ⁇ /8; 660K, 750 ⁇ /8; and 670K, ⁇ /s; respectively) showing the different types of failures; and
  • FIGs. 16A and 16B are images of an example blade that was machined to reveal a cross section.
  • the invention provides a method for making high quality blades in bulk metallic glass.
  • a supercooled material state is used to form a blade, e.g., via micromolding in a die.
  • the initial forming process can form blades of generally arbitraiy shape. Different rake angles can be formed.
  • the blade is then drawn to form an edge. Edge radiuses below -lOOnm can be formed, including edges in the range of ⁇ 5-100nm. Edges are suitable for surgeries, such as ophthalmological surgeries.
  • the bulk metallic glass blades formed in the invention are less expensive than state of the art diamond blades used for such surgeries as well as for other applications.
  • the bulk metallic glass is biocompatible.
  • a preferred process for manufacturing bulk metallic glass surgical blades uses thermally-assisted molding and drawing.
  • the shape and edge of the blade is created in a single simultaneous process that starts with blanks of bulk metallic glass, e.g., being rectangular in shape and of specific dimensions.
  • a high force precision mold is then used to form a rake face of the blade until only a small thickness of material remains at the edge. The remaining thickness is then drawn causing necking of the material until failure occurs along a fine edge.
  • Preferred processes of the invention can efficiently and economically manufacture surgical-grade blades.
  • the resulting bulk metallic glass blades have superior properties and higher performance than current metal alloys at a price point significantly lower than precision diamond blades.
  • an entire blade or plurality of blades are manufactured in a single two-stage process. This limits the handling of delicate pieces and chance for contamination along with increasing efficiency.
  • the process is very fast, requiring less than a minute to completely mold and draw the blade. Additionally, no timely post-processing like lapping is required to produce the final edge, saving time and money.
  • Several parameters can be easily adjusted to accommodate different metallic glasses or fine tune edge formation.
  • FIGs. 1A-1G illustrate a preferred embodiment process for fabricating a bulk metallic glass surgical grade blade of the invention.
  • a bulk metal glass sample 10 in FIG. lA has been heated to a supercooled temperature.
  • the heating can be accomplished through contact with an upper 12 and or lower die 14 or via other heating techniques such as environmental heating in a furnace chamber, resistive heating with electrical current, and immersion in liquid.
  • the heating through die contact may create desirable temperature gradients in material and is also preferred as a simple and inexpensive way to implement the preferred process.
  • One or both of the dies 12, 14 include a mold 16 for shaping a blade from the bulk metallic glass 10 while it is maintained in the supercooled state. Bringing the dies together such as by vertical movement of the upper die 12 provides an initial blade shape 18 in FIGs. IB and 1C.
  • the mold 16 obviously can be configured to form a plurality of blades simultaneously.
  • the blade 18 is drawn to deform the blade 18 and form a surgical grade edge 20 on the blade. This can be accomplished by moving the bulk metallic glass sample 10 in the horizontal direction as shown. Once the drawing is completed, the dies are moved apart from each other to release the final, finished blade, which does not require further processing or sharpening to form the desired edge radius
  • the process is capable of blades suitable for applications requiring the finest blade edge.
  • edges with a 14-100nm radius, and the experiments indicate that a 5nm radius edge can be achieved with optimization.
  • An endless variety of sizes and shapes can also be produced.
  • Typical blades of interest for surgical and scientific applications range from about l-4mm wide, 4-10 mm long and 200-500 ⁇ thick.
  • the shape, number of edges and angles can vary significantly between blade designs and the molding process can produce the necessary geometry for mounting to the blade to a handle either during the edge forming process or earlier when producing the initial material blanks prior to edge forming.
  • the bulk metallic glass 10 is a zirconium- based bulk metallic glass.
  • Bulk metallic glasses transition to a supercooled liquid state at high temperatures. This supercooled state allows the use of the present fabrication process with thermally-assisted shaping and drawing.
  • a preferred bulk metallic glass includes compositions having Zr, Ti, Cu, Ni, and Be, e.g., Zr 4) 25 Ti 13 7 5 Cui2.5NiioBe 2 2.5, which is available commercially under a brand called Vitreloy-1.
  • the onset of glass transition for Zr4j .25Tii 3 ,7 5Cui2.5 i 1( ⁇ Be 22 .5 has been previously determined to at 625 . However, significant softening of the material does not occur until around 650 .
  • the material has a relatively large stable supercooled region of about 80K where it follows a time/ temperature-dependent relation to ciystallization, which makes it very suitable for the present fabrication process.
  • Rapid cooling (1 K/s) during solidification from a melt allows the glass to reach a metastable condition in which the amorphous structure that existed in its liquid state is maintained, and it has a lower critical cooling rate to maintain its amorphous structure than most metallic glasses. It has an amorphous structure, high strength (1900 MPa) and high hardness (534 II V). The strength and hardness are equivalent to standard tool steels and are ideal for the formation and retention of a sharp edge. It reaches 2% elongation before failure at room temperature, which is greater than similar high strength brittle metals and ceramics. Additionally, Zirconium-based alloys have been shown to be fully biocompatible and unlike many plastic and silicon instruments, can be sterilized with any current medical method. See, L.
  • FIGs. lA-lF The drawing in FIGs. lA-lF is preferably conducted at a rate and a supercooled temperature that initially produces elastic deformation followed by plastic deformation with localized necking.
  • high temperatures in the supercooled range of the bulk metallic glass produce the desirable formation with higher drawing speeds, while lower temperatures in the supercooled regions work with lower drawing speeds. Optimizations for an example material are discussed below with respect to experiments.
  • FIG. 2 shows a micromolding system for forming bulk metallic glass surgical grade blades with the FIGs. 1 A-1F process. Items identified in FIGS. 1A- IF are given the same reference numbers in FIG. 2.
  • Two microactuators 22, 24 control the shaping and drawing processes.
  • the microactuators 22, 24 can be controlled by a computer program carried out by a microcontroller for molding and drawing a particular blade shape and bulk metallic glass material being processed.
  • the mold 16 is shown as a pair of die inserts. Die heaters 26 and 28 are embedded in the dies 12 and 14 and can likewise be controlled by a microcontroller that is programmed to carry out a particular molding and drawing operation with a given temperature and speed profile.
  • the bulk metallic glass sample 10 is held by an adaptor plate 30 attached to a load cell 32.
  • the load cell can be used to monitor force and as a check by a controller running a fabrication.
  • the upper die was controlled by a ball screw actuator capable of outputting over 1000N of force.
  • An LVDT Linear Variable Differential Transformer system
  • An additional actuator with sub-micron precision was used to draw the sample horizontally.
  • the critical geometries of both the upper and lower dies utilize tool steel mold inserts for maximum strength, higher precision and easy maintenance.
  • the lower die was adjustable to allow precise alignment of the upper and lower dies to create a uniform gap thickness during molding.
  • the upper die was designed to produce a 20° rake angle in the final blade. Heating is accomplished through resistive cartridge heaters placed within the upper and lower dies. Thermocouples are placed close to the die inserts to provide accurate temperature measurement. Temperature was regulated using a multi-channel PID controller providing an accuracy of ⁇ 1 .
  • the testbed was CNC-controlled.
  • Tests were conducted by clamping a sample in the adapter plate on the horizontal actuator. Next, the heating is activated and allowed to stabilize at the required operating temperature. At this point the CNC program is activated, which proceeds by first zeroing the upper die through contact to calibrate the LVDT. The actuator then moves the sample into the dies and pauses until the sample reaches the pre-specified operating temperature. Then the shaping and drawing are conducted as discussed above while the temperature is maintained at the predetermined temperature in the supercooled range.
  • the samples were 40 mm x 2 mm x 500 ⁇ (LxWxH). Multiple tests were run along the length of this sample, each test producing final blades roughly 3mm x 2mm x 500 ⁇ .
  • the upper die was stopped at a gap thickness of 20 ⁇ for all tests.
  • drawing force data was recorded to quantitatively analyze the deformation occurring in the sample.
  • a camera with a 200X microscope lens was used to provide a video record of each test in order to help visualize the deformation occurring during the test.
  • FIGs. 3-5 show the load cell force data from each test at the three different temperatures (650K, 660 , 670K).
  • the force is plotted versus the drawing distance.
  • Drawing distance is used to represent strain in the sample, since exact elongation was difficult to measure.
  • the varying response across each parameter is due to the combined strain rate and temperature dependence of bulk metallic glass within its supercooled region.
  • the material exhibits higher strength at both lower temperatures and higher feedrates.
  • the peak force for all the temperatures increases, but the drawing distance until failure quickly decreases.
  • the shape of the plot shifts from an almost flat line, to a gradual drop off, to eventually a quick rise and fall at the highest feedrates and lowest temperatures.
  • FIGs. 6A-6P are SEM images of a blade and blade edges formed during experiments.
  • FIG. 6A shows a complete blade.
  • FIGs. 6B-6P show the blade region highlighted in FIG. 6A.
  • FIG. 6B-6P have edges formed at different temperatures in Kelvin and feed rates in ⁇ s, and dotted lines indicate the point at which deformation began as a result of drawing.
  • the respective temperatures and feed rates were: FIG. 6B - 650/100; FIG. 6C - 650/250; FIG. 6D - 650/500; FIG. 6E - 650/750; FIG. 6F - 650/1000; FIG. 6G - 660/100; FIG. 6H - 660/250; FIG. 61 - 650/500; FIG.
  • FIG. 6J -660/750 FIG. 6K 660/1000; FIG. 6L - 670/100; FIG. 6M - 670/250; FIG. 6N - 670/500; FIG. 60 - 670/750; FIG. 6P - 670/1000.
  • the test at 650K and a feedrate of 1000 ⁇ /s shows one extreme where the material barely deforms before failing, exhibiting very rapid necking and only a small amount ( ⁇ 20 ⁇ ) of elongation before failing along a jagged edge.
  • a large amount of elongation occurs (600 ⁇ ) creating a weak, flimsy edge of very thin cross section ( ⁇ 1 ⁇ ).
  • the final edge may be of small radius, the blade structure directly behind the cutting edge is deemed insufficient to support the edge during cutting.
  • there is a balance between necking and elongation that produces a stable edge of small radius e.g. FlGs. 6B, 6C, 61, 6J, 6P.
  • FIG. 7 shows a plot of temperature versus feedrate for all tests with the results qualitatively assessed to be either good or poor. There appears to be a decidedly linear relation that defines the loci of temperature and feedrate combinations that produce good edges.
  • FIG. 8B shows a consistent trend of increasing force with either an increase in feedrate or a decrease in temperature. This follows the expected behavior of a Newtonian fluid.
  • the increase in force with feedrate is fairly linear across each temperature, except at 650K where the graph is slightly concave. This represents a shift towards non-Newtonian deformation and a decrease in viscosity with increasing strain rate. In addition to the change in force behavior, this shift towards non-Newtonian deformation has adverse effects on edge formation.
  • FIGs. 6D-6F where decreasing viscosity and a shift towards inhomogeneous deformation result in poor edge formation.
  • the material does not have sufficient time for structural relaxation to keep up with the rate of deformation.
  • the change in peak force versus temperature at a given feedrate is not linear, with a larger increase in force between 660 and 650 K, due to the non- linear relationship between viscosity and temperature.
  • FIG. 8C shows that the drawing distance is roughly bounded by 140 ⁇ on the low end due to elastic deformation in the bulk of the sample for the tests at 660 and 670 K.
  • FIG. 6F shows that the plastic deformation only occurs over about 30 ⁇ (the distance from the dashed line to the left edge). The highest elongation was seen at 650 K and a feedrate of 100 ⁇ /s where the material failed at a drawing distance of 1500 ⁇ . This is the extent to which the material can draw before the thickness becomes too thin and unstable. From FIG. 7 it appears that the best results occur at combinations of low temperatures and low feedrates as well as high temperatures and high feedrates. This corresponds to forces and elongations in FIGs. 8B and 8C, respectively, in the intermediate ranges of 25- 55N and 230 - 670 ⁇ .
  • Video from each test was synchronized with the drawing distance to characterize each stage of deformation and thereby better understand the deformation occurring.
  • Three distinct types of edge formation were seen and can be exemplified by the tests at 660 K and a feedrate of 100 ⁇ /s, 660 K and a feedrate of 1000 ⁇ /s, and 670 K and a feedrate of 750 ⁇ /s. They are elastic deformation, plastic deformation with no cross section reduction and plastic deformation with localized necking. During elastic deformation, the sample undergoes elastic elongation across its entire length. Plastic deformation with no cross section reduction is a result of the formation of a stable neck during the drawing of material.
  • the thickness of the material in the necked region does not significantly change, but large amounts of elongation can occur.
  • the material only deforms at the point of thinnest cross section and continues to reduce in area until failure.
  • FIG. 9 illustrates the type of deformation occurring for 660K and 100 ⁇ /s as a function of feree and drawing distance, and it is seen that there is a very small section of elastic deformation. Once a certain peak force is reached, the material begins to plastically deform over a large region (-800 ⁇ ) with very little reduction in cross section. After significant elongation has occurred the material eventually undergoes localized necking followed by failure (See FIGs. 6G, 6H, 6L, 6M, 6N).
  • FIGs. 10A- 10D are example images from the video of the 660 K and 100 ⁇ /s test at select drawing that was used to obtain the data in FIG. 9.
  • the first 100 ⁇ consist of elastic deformation indicated by the very small amount of change seen between FIGs. 10A and 10B. Between 100 ⁇ and 900 ⁇ the material elongates significantly with very little reduction in cross section, as seen in FIGs. IOC and 10D. Peak forces for this case are less than 25N and elongations are greater than 600 ⁇ . This case corresponds to the upper left hand corner of FIG. 7.
  • Plastic deformation with a constant cross section occurs in the necked region due to strain hardening in the material during deformation.
  • This hardening allows the formation of a stable neck causing further deformation to take place beyond the necked region and extend over a greater length.
  • This strain hardening is an effect generally caused by either crystalline structure or polymer chains in other materials, both of which are absent in bulk metallic glasses.
  • the strain hardening in this case is caused by nano-crystallization in the material during testing. In previous deformation studies, nano-crystallization was seen to occur if the material was held at a given temperature above the glass transition for an extended period of time. See, Q. Wang, S. Gravier, J.J. Blandin, J.M. Pelletier, J.
  • FIGs. 15A-15D show a selection of various edges formed under different temperatures and with different deformation rates showing the different types of failures.
  • FIG. ISA shows the edge formed after the type of deformation seen in FIG. 9. The edge is fairly uniform and homogeneous up until the failure, but the material is very thin and doesn't have a significant rake angle for stability.
  • FIG. 15B shows the edge formed after the deformation seen in FIG. 11. In this case, the necking and failure occurs so rapidly that little time is allowed for the material to homogeneously neck and deform to a single edge.
  • FIGs. 15C and 15D show edges formed from deformation similar to that in FIG. 13. In these cases, deformation follows a rate of necking that gives rise to the formation of a strong stable edge. However, the edge in FIG. 15D deformed more homogeneously before failure creating a more consistent and sharper edge than that of FIG. 15C, owing to the increase in temperature and feedrate.
  • FIG. 15D An FEI Dual Beam 235 FIB was used to perform focused ion beam machining on the sample shown in FIG. 15D to further analyze the edge radius.
  • the sample was initially coated with Au to prevent damage to the edge during ion milling, as well as, provide more contrast when viewed under SEM. Inside the FIB, the sample was then coated with Pt to further protect the edge during machining. Next, ion milling was used to cut a slot into the edge in order to view a cross section of the tip.
  • FIGs. 16A and 16B show the darker color within the dashed lines that represents the bulk metallic glass while the lighter portion is the Pt coating. From this image the edge radius can be estimated to be about 50 nm for this particular sample. Additional experiments guided by these results refined the edge radius to 14nm, and the experiments suggest that under the ideal conditions, the method could produce edges having a 5nm edge radius.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Materials For Medical Uses (AREA)

Abstract

Un mode de réalisation de l'invention concerne un procédé de fabrication d'une lame. Le procédé commence par chauffer du verre métallique massif jusqu'en un état de surfusion. Dans cet état, il est formé une lame en verre métallique massif. Elle est ensuite étirée, ce qui la déforme et forme sur la lame une arête de qualité chirurgicale. L'invention permet de former des lames de qualité chirurgicale en verre métallique massif dont une arête présente un rayon inférieur ou égal à ~100 nm et pouvant atteindre ~5 nm. L'arête de la lame fait la transition entre une zone de matériau présentant un resserrement localisé et un très petit rayon, ce qui garantit une lame de qualité chirurgicale robuste.
PCT/US2012/025903 2011-02-21 2012-02-21 Procédé de fabrication d'une lame et lame de qualité chirurgicale en verre métallique massif WO2012115944A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US201161444864P 2011-02-21 2011-02-21
US61/444,864 2011-02-21

Publications (1)

Publication Number Publication Date
WO2012115944A1 true WO2012115944A1 (fr) 2012-08-30

Family

ID=46721191

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/US2012/025903 WO2012115944A1 (fr) 2011-02-21 2012-02-21 Procédé de fabrication d'une lame et lame de qualité chirurgicale en verre métallique massif

Country Status (1)

Country Link
WO (1) WO2012115944A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10137487B2 (en) 2015-10-29 2018-11-27 Korea Institute Of Machinery & Materials Apparatus and method for manufacturing blade

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20050226955A1 (en) * 2004-04-09 2005-10-13 Seiji Yuasa Metallic mold for optical element and optical element
US20080034796A1 (en) * 2004-05-28 2008-02-14 Ngk Insulators, Ltd Method of Forming Metallic Glass
US20080155839A1 (en) * 2006-12-21 2008-07-03 Anderson Mark C Cutting tools made of an in situ composite of bulk-solidifying amorphous alloy
US20100098967A1 (en) * 2007-02-13 2010-04-22 Jan Schroers Method for Imprinting and Erasing Amorphous Metal Alloys

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20050226955A1 (en) * 2004-04-09 2005-10-13 Seiji Yuasa Metallic mold for optical element and optical element
US20080034796A1 (en) * 2004-05-28 2008-02-14 Ngk Insulators, Ltd Method of Forming Metallic Glass
US20080155839A1 (en) * 2006-12-21 2008-07-03 Anderson Mark C Cutting tools made of an in situ composite of bulk-solidifying amorphous alloy
US20100098967A1 (en) * 2007-02-13 2010-04-22 Jan Schroers Method for Imprinting and Erasing Amorphous Metal Alloys

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10137487B2 (en) 2015-10-29 2018-11-27 Korea Institute Of Machinery & Materials Apparatus and method for manufacturing blade

Similar Documents

Publication Publication Date Title
Mwangi et al. Nitinol manufacturing and micromachining: A review of processes and their suitability in processing medical-grade nitinol
Kaya et al. A review on machining of NiTi shape memory alloys: The process and post process perspective
Balázs et al. A review on micro-milling: recent advances and future trends
Venkatesh et al. Review on the machining characteristics and research prospects of conventional microscale machining operations
Zadafiya et al. Recent trends in non-traditional machining of shape memory alloys (SMAs): A review
Filiz et al. Micromilling of microbarbs for medical implants
Piquard et al. Micro-end milling of NiTi biomedical alloys, burr formation and phase transformation
Shunmugavel et al. A comparative study of mechanical properties and machinability of wrought and additive manufactured (selective laser melting) titanium alloy–Ti-6Al-4V
RU2720276C2 (ru) Термомеханическая обработка никель-титановых сплавов
Chen et al. Micro-machinability of bulk metallic glass in ultra-precision cutting
Kuriakose et al. Machinability study of Zr-Cu-Ti metallic glass by micro hole drilling using micro-USM
EP3202341B1 (fr) Ciseaux
Takale et al. Effect of wire electro discharge machining process parameters on surface integrity of Ti49. 4Ni50. 6 shape memory alloy for orthopedic implant application
Zainal Abidin et al. Chilled air system and size effect in micro-milling of nickel− titanium shape memory alloys
Santosh et al. An experimental analysis on the influence of CO2 laser machining parameters on a copper-based shape memory alloy
Krejcie et al. A hybrid process for manufacturing surgical-grade knife blade cutting edges from bulk metallic glass
Ray et al. Experimental analysis on the quality aspects of micro-channels in mechanical micro milling of Zr-based bulk metallic glass
Tian et al. The mechanism of anisotropic micro-milling properties in additively manufactured Ti-6Al-4V alloy
WO2012115944A1 (fr) Procédé de fabrication d'une lame et lame de qualité chirurgicale en verre métallique massif
Shunmugavel et al. Influence of build orientation on machinability of selective laser melted titanium alloy-Ti-6Al-4V
Alhadeff et al. The influence of tool coating on the length of the normal operating region (steady-state wear) for micro end mills
Takale et al. Multi-response optimization of micro-WEDM process parameters of Ti49. 4-Ni50. 6 shape memory alloy for orthopedic implant application
Falvo et al. Thermomechanical characterization of Nickel-Titanium shape memory alloys
Gowri et al. Micromachining: technology for the future
Behrens et al. Drawability of thin magnetron sputtered Al–Zr foils in micro deep drawing

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 12750294

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 12750294

Country of ref document: EP

Kind code of ref document: A1