RESEARCH
| REPORTS
two-dimensinal individual GO sheets (15, 18).
The physical entanglement and strong covalent
cross-links between graphitic planes may strongly
improve the mechanical properties of conven-
tional PAN-based carbon fibers and carbon nano-
tube fibers (15–17). Additionally, high-performance
carbon fibers and carbon nanotube fibers can
achieve more compact and more dense structures
(e.g., up to a theoretical density of 2.2 g/cm3 for
carbon fibers and thus minimized voids and de-
fects) (15, 16, 33).
High-performance carbon fibers are typical-
ly categorized into high-strength PAN-based
fibers and high-modulus mesophase pitch-based
carbon fibers (15, 16, 22). Thermal conductivity
is typically lower for PAN-based carbon fibers
because cross-linking atoms behave as scattering
centers to reduce phonon transport (15). A strong
correlation among the tensile strength, Young’s
modulus, and thermal and electrical conductiv-
ities was identified for mesophase pitch-based
carbon fibers (22). High-temperature carboniza-
tion allows the development and growth of the
crystalline graphitic domains and thus enables
simultaneously high modulus and high conduc-
tivities for mesophase pitch-based carbon fibers
(15, 22, 24). The superior thermal conductivity
but lower modulus of the optimized graphene
fibers as compared with mesophase pitch-based
carbon fibers is unexpected and could be attri-
buted to the unique fiber structure by intercalating
large- and small-sized graphene sheets and sub-
stantially larger crystalline domain sizes in both
transverse and longitudinal directions.
bright-field transmission electron microscope
images (fig. S6). These are orders of magnitude
larger than the nanocrystalline graphitic domains
(several tens of nanometers) inside the meso-
phase pitch-based and PAN-based carbon fibers
(15, 22, 32). Despite the relatively lower density,
the reduced phonon scattering from the bound-
ary and interface due to the larger-sized crystalline
domains enables more efficient phonon trans-
port and, thus, enhanced thermal conductivity.
The highly thermally conductive and mechani-
cally strong graphene fibers with intercalated
large- and small-sized graphene sheets have po-
tential for thermal management materials in
high-power electronics and reinforcing compo-
nents for high-performance composite materials.
15. X. Qin, Y. Lu, H. Xiao, Y. Wen, T. Yu, Carbon 50, 4459–4469
(2012).
16. K. Naito, Y. Tanaka, J.-M. Yang, Y. Kagawa, Carbon 46,
189–195 (2008).
17. N. Behabtu et al., Science 339, 182–186 (2013).
18. G. Xin et al., Adv. Mater. 26, 4521–4526 (2014).
19. C. Xiang et al., Adv. Mater. 25, 4592–4597 (2013).
20. L. Chen et al., Nanoscale 5, 5809–5815 (2013).
21. Materials and methods are available as supplementary
materials on Science Online.
22. F. G. Emmerich, Carbon 79, 274–293 (2014).
23. J.- Wang, M. Gu, W.- Ma, X. Zhang, Y. Song, New Carbon Mater.
23, 259–263 (2008).
24. N. C. Gallego et al., Carbon 38, 1003–1010 (2000).
25. A. F. Thünemann, W. Ruland, Macromolecules 33, 1848–1852
(2000).
26. A. Gupta, I. R. Harrison, J. Lahijani, J. Appl. Cryst. 27, 627–636
(1994).
27. C. Zhu et al., Carbon 50, 235–243 (2012).
28. S. Zhang et al., Nat. Mater. 9, 594–601 (2010).
29. L. Song et al., Carbon 52, 608–612 (2013).
30. S. Pei, H.-M. Cheng, Carbon 50, 3210–3228 (2012).
31. L. G. Cançado et al., Appl. Phys. Lett. 88, 163106 (2006).
32. M. Endo et al., Phys. Rev. B 58, 8991–8996 (1998).
33. J. N. Wang, X. G. Luo, T. Wu, Y. Chen, Nat. Commun. 5, 3848
(2014).
REFERENCES AND NOTES
1. A. A. Balandin, Nat. Mater. 10, 569–581 (2011).
2. W. Jang, Z. Chen, W. Bao, C. N. Lau, C. Dames, Nano Lett. 10,
3909–3913 (2010).
3. J. H. Seol et al., Science 328, 213–216 (2010).
4. C. Lee, X. Wei, J. W. Kysar, J. Hone, Science 321, 385–388
(2008).
ACKNOWLEDGMENTS
5. X. Du, I. Skachko, A. Barker, E. Y. Andrei, Nat. Nanotechnol. 3,
491–495 (2008).
This work is financially supported by the U.S. National Science
Foundation under awards DMR 1151028 and CMMI 1463083.
6. Z. Xu, C. Gao, Nat. Commun. 2, 571 (2011).
7. Z. Xu, C. Gao, Acc. Chem. Res. 47, 1267–1276 (2014).
8. Z. Xu, H. Sun, X. Zhao, C. Gao, Adv. Mater. 25, 188–193 (2013).
9. H.-P. Cong, X.-C. Ren, P. Wang, S.-H. Yu, Sci. Rep. 2, 613
(2012).
10. M. K. Shin et al., Nat. Commun. 3, 650 (2012).
11. X. Hu, Z. Xu, Z. Liu, C. Gao, Sci. Rep. 3, 2374 (2013).
12. C. Xiang et al., ACS Nano 7, 1628–1637 (2013).
13. Z. Xu, Z. Liu, H. Sun, C. Gao, Adv. Mater. 25, 3249–3253 (2013).
14. P. M. Adams, H. A. Katzman, G. S. Rellick, G. W. Stupian,
Carbon 36, 233–245 (1998).
SUPPLEMENTARY MATERIALS
Materials and Methods
Supplementary Text
Figs. S1 to S8
Table S1
References (34–40)
8 January 2015; accepted 30 July 2015
10.1126/science.aaa6502
For graphene-based materials, heat conduc-
tion is dominated by phonon transport from
lattice vibrations of the covalent sp2 bonding
network, and the electron transport is largely
determined by the delocalized p-bond over the
whole graphene sheet (1, 3, 18, 30). The lattice
vacancies and the residual functional groups on
graphene sheets upon thermal reduction create
substantial numbers of phonon- and electron-
scattering centers, significantly degrading the
thermal and electrical properties (1, 3, 18, 30).
High-temperature annealing heals defects in
the lattice structure and removes oxygen func-
tional groups and significantly increases the
size of the sp2 domains (fig. S6). The crystallite
sizes (Fig. 4F) in parallel and perpendicular di-
rections to the fiber axis have been calculated
from the integrated intensity ratios of the D-
band (1350 cm−1) and the G-band (1581 cm−1)
based on polarized Raman spectra of the opti-
mized graphene fibers annealed at different tem-
peratures (Fig. 4E and fig. S8) (31, 32). At lower
annealing temperatures (e.g., 1800°C), graphene
fibers demonstrate smaller-sized sp2 domains
(40 to 50 nm) with residual defects. The domain
sizes of the optimized graphene fibers in both
longitudinal and transverse directions increase
substantially with the annealing temperature
(Fig. 4F) and approach 783 and 423 nm, respec-
tively, upon annealing at 2850°C. This is further
evidenced by the submicrometer-sized crystal-
line domains along the fiber axis for the high
temperature–treated fibers as observed in the
CATALYSIS
Sustainable Fe–ppm Pd nanoparticle
catalysis of Suzuki-Miyaura
cross-couplings in water
Sachin Handa,1 Ye Wang,1 Fabrice Gallou,2 Bruce H. Lipshutz1*
Most of today’s use of transition metal–catalyzed cross-coupling chemistry relies on
expensive quantities of palladium (Pd). Here we report that nanoparticles formed from
inexpensive FeCl3 that naturally contains parts-per-million (ppm) levels of Pd can catalyze
Suzuki-Miyaura reactions, including cases that involve highly challenging reaction partners.
Nanomicelles are employed to both solubilize and deliver the reaction partners to the
Fe–ppm Pd catalyst, resulting in carbon-carbon bond formation. The newly formed catalyst
can be isolated and stored at ambient temperatures. Aqueous reaction mixtures
containing both the surfactant and the catalyst can be recycled.
recious metal catalysis has been and con-
tinues to be a predominant means of C-C,
C-H, and C-heteroatom bond construc-
tion in organic synthesis. In particular,
palladium-catalyzed Suzuki-Miyaura, Heck,
and Negishi couplings are indispensable, as rec-
ognized by the 2010 Nobel Prize (1, 2). However,
economically accessible supplies of Pd and other
precious metals are dwindling, thus raising con-
cerns about the sustainability of this chemistry (3).
To circumvent this situation, alternative metals
such as nickel (4, 5) and copper (6, 7) have been
studied, especially as applied to the heavily used,
Pd-catalyzed Suzuki-Miyaura reactions (8, 9). De-
spite varying degrees of success, Pd remains, by
P
1Department of Chemistry and Biochemistry, University of
California–Santa Barbara, Santa Barbara, CA 93106, USA.
2Novartis Pharma, Basel, Switzerland.
*Corresponding author. E-mail: lipshutz@chem.ucsb.edu
SCIENCE sciencemag.org
4 SEPTEMBER 2015 • VOL 349 ISSUE 6252 1087