• No se han encontrado resultados

CAPÍTULO 5: CONCLUSIONES

4. Trabajo futuro

Conocido todo esto, si una vez realizados los estudios de las propiedades mecánicas de los cementos óseos con copolímeros de bloque, se observa que estas mejoran notablemente, fundamentalmente la tenacidad a la fractura, lo lógico sería estudiar la posibilidad de añadir al cemento óseo nanotubos (en torno al 0.5%) y Nanostrenght®M52 de manera simultánea. De esta manera es posible que los nanotubos

108 mejoren las propiedades térmicas, mientras que el Nanostrenght® M52 mejora las propiedades mecánicas.

A su vez, también se pretende trabajar con otros copolímeros en bloque con distintas estructuras para comprobar su efecto sobre los cementos.

109

Bibliografía

[ANDR02] Andrews R, Jacques D, Qian D, Rantell T. Multiwall carbon nanotubes: synthesis and application. Acc Chem Res. 2002 Dec;35(12):1008-17.

[ANDR04] Andrews R. and Weisenberger M.C. (2004). Carbon nanotube polymer composites, Curr. Opin. Solid State & Mat. Sc., 8:31-37.

[CHAN06] Chandler M, Kowalski RS, Watkins ND, Briscoe A, New AM. Cementing techniques in hip resurfacing. Proc Inst Mech Eng H. 2006 Feb;220(2):321-31.

[CHAR75] Charnley J. Fracture of femoral prostheses in total hip replacement. AClinical Study. Clin orthop. 1975;111: 105-120.

[CHEN12] Chen J, Taylor A. Mechanical and fracture behavior of triblock copolymer modified high crosslink density epoxy. In the Annual Meeting of The Adhesion Society 2012.

[DELM05] Delmas, A (11a ed. 2005). Anatomía topográfica del miembro inferior. En Rouvière, H. Delmas, V. Anatomía Humana Descriptiva, topográfica y funcional. Tomo 3. Miembros. (736 págs).

[DELR12] Del Real JC, Abenojar J, Cledera MM, Forriol F, Martínez MA. Evaluation of the influence of the addition of Vancomycin and Cefazolin on polymerization kinetics of acrylic bone cement. In the Annual Meeting of The Adhesion Society 2012. [DEMC02] Demczyk BG, Wang YM, Cumings J. Direct mechanical measurement of the tensile strength and elastic modulus of multiwalled carbon nanotubes. Materials Science and Engineering A. 2002;334(1-2):173-178

[DUNN02] Dunne NJ, Orr JF. Curing characteristics of acrylic bone cement. J Mater Sci Mater Med. 2002 Jan;13(1):17-22.

[DUNN03] Dunne NJ, Orr JF, Mushipe MT, Eveleigh RJ. The relationship between porosity and fatigue characteristics of bone cements. Biomaterials. 2003 Jan;24(2):239- 45.

[DUNN11] Dunn N, Ormsby RW. (2011). MWCNT Used in Orthopaedic Bone Cements, Carbon Nanotubes - Grom/mh and Applications, Dr. Mohammad Naraghi (Ed.), ISBN: 978-953-307-566-2, InTech, Available from:

http://www.intechopen.com/books/carbon-nanotubes-grom/mh-and- applications/mwcnt-used-in-orthopaedic-bone-cements.

[FRAN05] Franklin P, Wood DJ. and Bubb NL. Reinforcement of

poly(methylmethacrylate) denture base with glass flake. Dental Materials 2005; 21(4): 365-370.

110 [FUKU02] Fukushima H, Hashimoto Y, Yoshiya S, Kurosaka M, Matsuda M,

Kawamura S, Iwatsubo T. Conduction analysis of cement interface temperature in total knee arthroplasty. Kobe J Med Sci. 2002 Apr;48(1-2):63-72.

[GILB00] Gilbert JL, Hasenwinkel JM, Wixson RL, Lautenschlager EP. A theoretical and experimental analysis of polymerization shrinkage of bone cement: A potential major source of porosity. J Biomed Mater Res. 2000 Oct;52 (1):210-8.

[HARP00] Harper EJ, Bonfield W. Tensile characteristics of ten commercial acrylic bone cements. J Biomed Mater Res. 2000 Sep;53(5):605-16.

[HULL96] Hull D, Clyne TW. Fibres and matrices. An Introduction to Composite Materials. Clarke DR, Cambridge University Press: 9-38. (1996).

[ISO02] ISO 5833:2002 Implants for surgery - Acrylic resin cements. International Standard Organization

[JAST91] Jasty M, Maloney WJ, Bragdon CR, O'Connor DO, Haire T, Harris WH. The initiation of failure in cemented femoral components of hip arthroplasties. J Bone Joint Surg Br. 1991 Jul;73 (4):551-8.

[KOTH06] Kotha SP, Li C, McGinn P, Schmid SR and Mason JJ. Improved mechanical properties of acrylic bone cement with short titanium fiber reinforcement. Journal of Materials Science: Materials in Medicine 2006;17(8): 743-8.

[KUEH05] Kuehn KD, Ege W, Gopp U. Acrylic bone cements: composition and properties. Orthop Clin North Am. 2005 Jan;36(1):17-28, v. Review.

[LACR00] Lacroix D, Murphy LA, Prendergast PJ. Three-dimensional finite element analysis of glenoid replacement prostheses: a comparison of keeled and pegged anchorage systems. J Biomech Eng. 2000 Aug;122(4):430-6.

[LARS91] Larsen ST, Franzen S, Ryd L. Cement interface temperature in hip arthroplasty. Acta Orthopaedica Scandinavica. 1991;62(2):102-105

[LENN02] Lennon AB, Prendergast PJ. Residual stress due to curing can initiate

damage in porous bone cement: experimental and theoretical evidence. J Biomech. 2002 Mar;35(3):311-21.

[LEWI03] Lewis G, Janna S, Carroll M. Effect of test frequency on the in vitro fatigue life of acrylic bone cement. Biomaterials. 2003 Mar;24(6):1111-7.

[LEWI04] Lewis G, Janna SI. Effect of fabrication pressure on the fatigue performance of Cemex XL acrylic bone cement. Biomaterials. 2004 Mar-Apr;25(7-8):1415-20. [LEWI97] Lewis G. Properties of acrylic bone cement: state of the art review. J Biomed Mater Res. 1997 Summer;38(2):155-82. Review.

111 [LIDG87] Lidgren L, Bodelind B, Möller J. Bone cement improved by vacuum mixing and chilling. Acta Orthop Scand. 1987 Feb;58(1):27-32.

[LIJI91] Iijima S. Helical microtubules of graphitic carbon, Nature (London), 1991, 354, 56-58

[MARR06] Marrs B, Andrews R, Rantell T. Augmentation of acrylic bone cement with multiwall carbon nanotubes. Journ Biomed Mat Res Part A. 2006;77(A):269-276 [MCCL10] McClory C, McNAlly T, Baxendale M. Electrical and rheological percolation of PMMA/MWCNT composites as a function of CNT geometry and functionality. European Polymer Journal. 2010;46(5):854-868

[MEYE73] Meyer PR Jr, Lautenschlager EP, Moore BK. On the setting properties of acrylic bone cement. J Bone Joint Surg Am. 1973 Jan;55(1):149-56. No abstract available.

[MOUS00] Mousa WF, Kobayashi M, Shinzato S, Kamimura M, Neo M, Yoshihara S, Nakamura T. Biological and mechanical properties of PMMA-based bioactive bone cements. Biomaterials. 2000 Nov;21(21):2137-46

[NORM95] Norman TL, Kish V, Blaha, JD, Gruen TA. and Hustosky K. Creep

characteristics of hand-mixed and vacuum-mixed acrylic bone-cement at elevated stress levels." Journal of Biomedical Materials Research 1995; 29(4): 495-501.

[NUÑOa02] Nuño N, Amabili M. Modelling debonded stem-cement interface for hip implants: effect of residual stresses. Clin Biomech (Bristol, Avon). 2002 Jan;17 (1):41- 8.

[NUÑOb02] Nuño N, Avanzolini G. Residual stresses at the stem-cement interface of an idealized cemented hip stem. J Biomech. 2002 Jun;35(6):849-52.

[ORMS10a] Ormsby R, McNally T, Mitchell C, Dunne N. Incorporation of multiwalled carbon nanotubes to acrylic based bone cements: effects on mechanical and thermal properties. J Mech Behav Biomed Mater. 2010 Feb;3(2):136-45. Epub 2009 Oct 13. [ORMS10b] Ormsby R, McNally T, Mitchell C, Dunne N. Influence of multiwall carbon nanotube functionality and loading on mechanical properties of

PMMA/MWCNT bone cements. J Mater Sci Mater Med. 2010 Aug;21(8):2287-92. Epub 2009 Dec 20.

[ORMS11] Ormsby R, McNally T, O'Hare P, Burke G, Mitchell C, Dunne N. Fatigue and biocompatibility properties of a poly(methyl methacrylate) bone cement with multi- walled carbon nanotubes. Acta Biomater. 2012 Mar;8(3):1201-12. Epub 2011 Oct 13. [ORR03] Orr JF, Dunne NJ, Quinn JC. Shrinkage stresses in bone cement.

112 [PAZ10] Eva Paz, Julian Narbón, Juan Carlos del Real; Analisis de la influencia de la viscosidad de un adhesivo acrílico en su capacidad de mojado y su repercusión en la resistencia de la unión,(2010)

[PILL76] Pilliar RM, Blackwell R, Macnab I and Cameron HU. Carbon fiber reinforced bone cement in orthopedic surgery. Journal of Biomedical Materials Research 1976;10(6): 893-906.

[PUKA05] Pukansky, B. - European Polymer Journal, 41, p.645, 2005.

[ROBI81] Robinson RP, Wright TM and Burstein AH. Mechanical properties of poly(methyl methacrylate) bone cements. Journal of Biomedical Materials Research 1981);15(2): 203-208.

[ROQU04] Roques A, Browne M, Taylor A, New A, Baker D. Quantitative measurement of the stresses induced during polymerisation of bone cement. Biomaterials. 2004 Aug;25(18):4415-24.

[ROUV05] Rouvière, H. (11a ed. 2005). Articulaciones del miembro inferior. En Rouvière, H.; Delmas, A.; Delmas, V. Anatomía Humana Descriptiva, topográfica y funcional. Tomo 3. (736 págs).

[SAHA86] Saha S and Pal S. Mechanical characterization of commercially made carbonfibrereinforced polymethylmethacrylate. Journal of Biomedical Materials Research 1986;20(6): 817-826.

[SAND11 ] Sandoo A, Veldhuijzen van Zanten JJ, Metsios GS, Carroll D, Kitas GD. Vascular function and morphology in rheumatoid arthritis: a systematic review. Rheumatology (Oxford). 2011 Nov;50(11):2125-39. Epub 2011 Sep 16.

[SAUE80] Sauer JA, Richardson GC. Fatigue of polymers. International Journl of Fracture. 1980: 16 (6): 499-532.

[SCHE00] Scheirs J, De Bruyn L, Verhagen R. Optimization of adult performance determines host choice in a grass miner.Proc Biol Sci. 2000 Oct 22;267(1457):2065-9. [SERB04] Serbetci K, Korkusuz F and Hasirci N. Thermal and mechanical properties of hydroxyapatite impregnated acrylic bone cements. Polymer Testing 2004;23(2): 145-55. [SEST84] Šesták J.Thermal analysis: Part D: Thermophysical properties of solids. Journal of Polymer Science: Polymer Letters Edition. 1984; 22(12): 675–676

[SHIN00] Shinzato S, Kobayashi M, Mousa WF, Kamimura M, Neo M, Kitamura Y, Kokubo T and Nakamura T. Bioactive polymethyl methacrylate-based bone cement: Comparison of glass beads, apatite- and wollastonite-containing glass ceramic, and hydroxyapatite fillers on mechanical and biological properties. Journal of Biomedical Materials Research 2000;51(2): 258-272.

113 [STAN04] Stanczyk M, van Rietbergen B. Thermal analysis of bone cement

polymerisation at the cement-bone interface. J Biomech. 2004 Dec;37(12):1803-10. [STOL04] Stolk J, Verdonschot N, Murphy BP, Prendergast PJ. Rik Huiskes.Finite element simulation of anisotropic damage accumulation and creep in acrylic bone cement. Engineering Fracture Mechanics 2004;71: 513-528.

[TEJE98] Tejerina T, Ganado P. Reacción fármaco-dinámica entre el cemento óseo y el tejido vascular. Anales de la Real Academia de Doctores 1998. (2): 56-65.

[TOPO90] Topoleski LD, Ducheyne P, Cuckler JM. A fractographic analysis of in vivo poly(methyl methacrylate) bone cement failure mechanisms. J Biomed Mater Res. 1990 Feb;24(2):135-54.

[TOPO93] Topoleski LD, Ducheyne P, Cuckler JM. Microstructural pathway of fracture in poly(methyl methacrylate) bone cement. Biomaterials. 1993

Dec;14(15):1165-72.

[TOPO98] Topoleski LD, Ducheyne P and Cuckler JM. Flow intrusion characteristics and fracture properties of titanium-fibre-reinforced bone cement. Biomaterials

1998;19(17): 1569-1577.

[VERD97] Verdonschot N, Huiskes R. The effects of cement-stem debonding in THA on the long-term failure probability of cement. J Biomech. 1997 Aug;30(8):795-802. [WAGN10] M. Wagner, L.M. Lu. Thermal Analysis in Practice. DongHua University Press, Shang Hai (2010).

[WONG97] Wong EW, Sheehan PE, Lieber CM. Nanobeam mechanics: elasticity, strength and toughness of nanorods and nanotubes. Science 1997;277(5334):1971-5 [WRIG82] Wright TM and Robinson RP. Fatigue crack propagation in poly

methylmethacrylate bone cements. Journal of Materials Science 1982;17(9): 2463-8. [XIE05] Xie XL, Mai YW, Shou XP. Dispersion and alignment of carbon nanotubes in polymer matrix: A review. Material Science Engineering. 2005;49(4):89-112

[YANG97] Yang JM, Huang PY, Yang MC. and Lo SK. Effect of MMA-g- UHMWPE grafted fiber on mechanical properties of acrylic bone cement. Journal of Biomedical Materials Research 1997;38(4): 361-369.

[ZHAN98] Zhang Y, Suenaga K, Colliex C, Iijima S. Coaxial nanocable: silicon carbide and silicon oxide sheathed with boron nitride and carbon . Science. 1998 Aug 14;281(5379):973-5.

115

Thin Multi-Wall Carbon Nanotubes

Nanocyl®-7000 series thin multi-wall carbon nanotubes are produced via the catalytic carbon vapor deposition (ccvd) process.

A primary interest is in applications requiring low electrical percolation threshold such as high-performance electrostatic dissipative plastics or coatings.

Nanocyl®-7000 is available in powder form in quantities starting at 1 kg to multi-tons. Pre-dispersed forms are also available (PlastiCylTM, EpoCylTM, AquaCylTM).

Ref: NC7000DS - 05 February 2007

Characterization Nanocyl®-7000

Property Unit Value Method of Measurement

Average diameter nanometers 9.5 TEM Average Length microns 1.5 TEM Carbon Purity % 90 TGA Metal Oxide (impurity) % 10 TGA Amorphous Carbon & Carbon

Shells (impurity) % Not detectable HRTEM Surface area m2/g 250-300 BET

+ Further information is available upon request

The information contained on this datasheet is believed to be reliable— yet Nanocyl makes no warranties and assumes no liability in connection with any use of this information. Nothing herein is to be taken as a license to operate under or infringe any patent. While this information is accurate at the time of publication, please contact Nanocyl or check http://www.nanocyl.com for the most up-to-date information.

Nanocyl S.A. Rue de l’Essor, 4 B-5060 Sambreville BELGIUM Tel +32 71 750 380 Fax +32 71 750 390 [email protected]

www.nanocyl.com

US Offices 800 Hingham St. Rockland MA 02370 U.S.A. Tel +1 781 261 9778 Fax +1 781 261 9769 [email protected]

The Carbon Nanotube Specialist

Nano-engineer your future

Technical Data Sheet- Nanostrength M52 for Epoxies

February 2011 1

NANOSTRENGTH

M52

EPOXY APPLICATION

TECHNICAL DATA SHEET

Description:

Nanostrength M52 is a PMMA-bloc-PbuA-bloc-PMMA copolymer. As for the Nanostrength range, the Nanostrength M52 is particularly well suited when toughening is required while maintaining the thermal properties of the thermoset sytems.

The Nanostrength M52 has been specifically designed to provide excellent properties in low polar thermoset systems like Epoxy-Jeffamine, Epoxy-MDEA or Epoxy-phenolics.

Typical dosages range from 3 to 10% for toughening. At higher loadings (15-50%), Nanostrength® modifies the rheology to allow innovative automated solvent free processing of thermoset systems.

Key features:

Nanostrength M52 has the following key characteristics

(1)

Data not intended for specification purposes

Benefits and applications:

Nanostrength® is a new family of self-assembling block copolymers. They are constituted of three blocks of linear chains covalently bonded to one another. The family currently consists in two categories: the SBM and the MAM. SBM are constituted of polystyrene, 1,4-polybutadiene and syndiotactic poly(methyl methacrylate) whereas MAM are pure acrylic symmetric block copolymers constituted of a center block of poly(butyl acrylate) and two side blocks of poly(Methyl methacrylate). Because of repulsive interactions between the three blocks, Nanostrength self-organize at the nanometer scale. Blended with a polymer compatible with one of their blocks, Nanostrength disperse easily and impose a structuration to the host matrix. This organization imparts unique combinations of properties, such as impact strength, high rigidity and transparency.

Thanks to the BlocBuilder technology, all the Nanostrength MAM are free of any metal or halogen species. Nanostrength M52 represents a very interesting balance between toughness and viscosity for DGEBA- Jeffamine systems. It also gives unique properties in TGDDM-MDEA systems.

Property Method Unit Typical value (1)

Aspect Visual White powder Rubber content Medium

Polarity Standard

EEW ISO 3001 g/Eq 0 Viscosity at 10% in

DGEBA LY556 at 80°C Rheometer mPa.s 560 MFI 190°C, 2.16kg 5 Thermal stability TGA under N2 °C > 300°C

Technical Data Sheet- Nanostrength M52 for Epoxies February 2011 2 Viscosity 0,01 0,1 1 10 100 20 40 60 80 100 120 140 Temperature (°C) V is c o s it y ( P a .s ) DGEBA 10% M52 Mechanical properties Example of a stress-strain curve* for TGDDM-MDEA system modified with 10% of M52.

*)

The curve is intended solely for indicating potential performance that can be achieved with Nanostrength M52 but it doesn’t replace the reader’s own evaluations and experimentation 0 10 20 30 40 50 60 70 80 90 0 1 2 3 4 5 Strain (%) S tr e s s ( M P a ) Systems KIC (MPa.m 0.5 ) GIC (J.m²) Tg (°C) TGDDM-MDEA 0.76 180 167 + 10% M52 1.53 784 171 RTM 6 0.64 - 231 + 5% M52 0.9 - 230 Example of the temperature

dependence of the viscosity* of an Epoxy/M52 90/10 mixture.

*)

The curve is intended solely for indicating potential performance that can be achieved with Nanostrength M52 but it doesn’t replace the reader’s own evaluations and experimentation

Technical Data Sheet- Nanostrength M52 for Epoxies

February 2011 3

Lap Shear results in a DGEBA-DETA system

0 2 4 6 8 10 12 14 16 18 Reference 10% Nanostrength M52 S tr e s s a t b re a k ( M P a ) -40°C Room Temp 80°C Morphology TGDDM-MDEA Opaque

Technical Data Sheet- Nanostrength M52 for Epoxies

February 2011 4

For thermoset applications, Nanostrength® are offered in powder forms. The powders can be dissolved in many epoxy precursors by heating/stirring process (typically between 80 and 150°C)

Indicative dissolution time in DGEBA LY556

The dissolution is estimated when 90% of the torque is reach, using a classical reactor as a mixing device.

Dissolution Temperature

90°C 135°C

Dissolution time (min) 25 2

A typical dissolution procedure (e.g: LY556 (Huntsman) and 10% of Nanostrength) is as follow:

- Thicken the epoxy at room temperature by gently stirring the Nanostrength powder. This technique should avoid the agglomeration of the powder that can occur when it is added in the hot epoxy.

- Heat the mixture at the appropriated temperature (often in the 90 - 160°C range: see table 1) and continue slow stirring until complete dissolution. This step can be done under vacuum.

- When the Nanostrength is dissolved, the temperature can be decrease (if necessary) and the hardener added.

In some system such as bis aniline (e.g: MDEA, MMPI…), it is advantageous to dissolve the Nanostrength powder in the curing agent and then to add the epoxy precursor in the blend (before it recrystallizes).

Trends of solubility:

The best solubility occurs in liquid bisphenol A epoxy (DGEBA). When the molecular weight of the DGEBA is increased (type 1 to 9), the solubility of the Nanostrength is slightly decreased. The consequence is that the time to solubilize the Nanostrength in a liquid/solid epoxy system can be slightly higher than in a pure low viscosity liquid epoxy.

Solvent based applications

Nanostrength® M52 is soluble in many common organic solvents (toluene, methyl ethyl ketone (MEEK), dimethylformamide (DMF), tetrahydrofuran (THF), acetone and methoxyethanol).

Reactive diluents

Reactive diluents are also excellent solvent for the Nanostrength® powder. Nanostrength® can be dissolved first in the reactive diluents or in the mixture of epoxy/reactive diluents. They allow a great decrease of the viscosity of the epoxy/Nanostrength solution.

Bubbles formation/Degazing step:

To avoid bubbles formation, it is easier to work at low shear rate rather than high shear rates. Because Nanostrength are dissolved and not dispersed, a high shear is also not recommended.

A degazing step can be necessary in some case to remove some bubbles. For a better efficiency, the degazing step should be done at the highest possible temperature.

Technical Data Sheet- Nanostrength M52 for Epoxies

February 2011 5

Nanostrength® M52 is provided in 20kg bags.

Nanostrength® M52 should be stored in a dry place, protected from light. It should be stored below 70°C to avoid any alteration of the product.

If the bags have been opened for a long time, a drying of the Nanostrength® might be necessary. Typical conditions are one night at 60°C under vacuum.

Safety and Handling:

Please refer to the Safety Data Sheet

Contacts:

www.nanostrength.com

[email protected]

The information contained in this document is based on trials carried out by our Research Centers and data selected from the literature, but shall in no event be held to constitute or imply any warranty, undertaking, expressed or implied commitment from our part. Our formal specifications define the limit of our commitment. No liability whatsoever can be accepted by Arkema with regard to the handling, processing, or use of the product or products concerned - which must in all cases be employed in accordance with all relevant laws and/or regulations in force in the country or countries concerned.

The statements, technical information, and recommendations contained herein are believed to be accurate as of the date hereof. Since the conditions and methods of use of the product and of the information referred to herein are beyond our control, ARKEMA expressly disclaims any and all liability as to any results obtained or arising from any use of the product or reliance on such information; NO WARRANTY OF FITNESS FOR ANY PARTICULAR PURPOSE, WARRANTY OF MERCHANTABILITY OR ANY OTHER WARRANTY, EXPRESSED OR IMPLIED, IS MADE CONCERNING THE GOODS DESCRIBED OR THE INFORMATION PROVIDED HEREIN. The information provided herein relates only to the specific product designated and may not be applicable when such product is used in combination with other materials, or in any process. The user should thoroughly test any application before commercialization. Nothing contained herein constitutes a license to practice under any patent and it should not be construed as an inducement to infringe any patent and the user is advised to take appropriate steps to be sure that any proposed use of the product will not result in patent infringement. See MSDS for Health & Safety Considerations.

Documento similar