Texture formation of hot-deformed nanocomposite Nd2Fe14B/α-Fe magnets by Nb and Zn additions
Transcript of Texture formation of hot-deformed nanocomposite Nd2Fe14B/α-Fe magnets by Nb and Zn additions
Texture formation of hot-deformed nanocomposite Nd2Fe14B/α-Fe magnets by Nb andZn additionsY. L. Ma, Q. Shen, X. B. Liu, Y. Qiu, C. H. Li, A. R. Zhou, J. C. Sun, and D. M. Chen Citation: Journal of Applied Physics 115, 17A704 (2014); doi: 10.1063/1.4860942 View online: http://dx.doi.org/10.1063/1.4860942 View Table of Contents: http://scitation.aip.org/content/aip/journal/jap/115/17?ver=pdfcov Published by the AIP Publishing Articles you may be interested in Anisotropic hot deformed magnets prepared from Zn-coated MRE-Fe-B ribbon powder (MRE=Nd+Y+Dy) J. Appl. Phys. 115, 17A725 (2014); 10.1063/1.4866086 Electrical and magnetic properties of hot-deformed Nd-Fe-B magnets with different DyF3 additions J. Appl. Phys. 114, 133902 (2013); 10.1063/1.4822026 Enhanced texture in die-upset nanocomposite magnets by Nd-Cu grain boundary diffusion Appl. Phys. Lett. 102, 072409 (2013); 10.1063/1.4793429 Textured Nd2Fe14B flakes with enhanced coercivity J. Appl. Phys. 111, 07A735 (2012); 10.1063/1.3679425 Enhanced coercivity in thermally processed ( Nd , Dy ) ( Fe , Co , Nb , B ) 5.5 ∕ α - Fe nanoscale multilayermagnets J. Appl. Phys. 97, 104308 (2005); 10.1063/1.1905788
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Texture formation of hot-deformed nanocomposite Nd2Fe14B/a-Fe magnetsby Nb and Zn additions
Y. L. Ma,1,2,a) Q. Shen,3 X. B. Liu,2 Y. Qiu,1 C. H. Li,1 A. R. Zhou,1 J. C. Sun,1
and D. M. Chen1
1College of Metallurgical and Materials Engineering, Chongqing University of Science and Technology,Chongqing 401331, China2Department of Physics, University of Texas at Arlington, Arlington, Texas 76019, USA3College of Materials Science and Engineering, Chongqing University of Technology, Chongqing 400054,China
(Presented 5 November 2013; received 23 September 2013; accepted 14 October 2013; published
online 9 January 2014)
The effect of Zn addition on the magnetic properties and microstructure of bulk hot-deformed
(NdDy)11.5Fe82.5�xNbxB6 (x¼ 0–2) alloys has been investigated. The remanence (Br) and coercivity
(Hci) can be enhanced substantially by the addition of Nb and can be further improved by the
combined addition of Nb and Zn. The addition of Nb increases the volume fraction of intergranular
phase and promotes more Zn to diffuse into the grain boundary. This grain boundary with changed
properties may benefit the c-axis texture formation during hot-deformation. Additionally, the
coercivity of alloys with both Nb and Zn increased up to 22% with increasing deformation ratio,
which may be due to the further diffusion of Zn into the grain boundary and the enhancement of
magnetic decoupling effect between Nd2Fe14B grains. VC 2014 AIP Publishing LLC.
[http://dx.doi.org/10.1063/1.4860942]
Bulk anisotropic nanocomposite RE2Fe14B/a-Fe (RE is
rare earth) alloys have attracted considerable interests due to
their lower rare earth content and higher theoretical energy
product than conventional RE-Fe-B.1,2 However, it is still a
great challenge to obtain bulk anisotropic nanocomposite alloys
with good magnetic properties by hot-deformation since little
RE-rich phase is contained, which is important to the develop-
ment of aligned platelet-shaped grains with c-axis parallel to
the press direction.3–5
In order to enhance the formation of c-axis texture in the
RE-lean precursor, many efforts have been made by applying
various methods, such as blending RE-rich melt-spun pow-
ders with RE-lean or a-Fe powders and a severe hot
deformation.6–9 Among the various methods, the additions
of low melting-point elements have been proved to be effec-
tive in greatly improving the texture development in RE-lean
precursor. Lee et al. and Gabay et al. obtained the bulk ani-
sotropic nanocomposite RE-Fe-B magnets by applying the
hot deformation combined with Cu and Al additions.10,11
The maximum energy product [(BH)m] of 37.3 MGOe was
obtained by hot-deformation and blending melt-spun powder
of MQP-15-7 with Nd-Cu powder.12 Moreover, our previous
studies have shown that Zn addition can improve the micro-
structure and magnetic properties of hot-deformed (HD)
nanocomposite RE-Fe-Nb-B magnets.13,14 However, Li
et al. found that the texture and magnetic properties of bulk
anisotropic RE-lean alloys can be also enhanced by Nb dop-
ing, which has a very high melting-point.15 To clarify the
effects of element additions on the evolution of microstruc-
ture and magnetic properties, the Nb doping, and Zn addition
in hot-deformed nanocomposite magnets have been investi-
gated in this work.
Alloy ingots of (NdDy)11.5Fe81.5�xNbxB6 (x¼ 0, 0.5, 1,
1.5, 2) prepared by induction melting were melt-quenched
onto a copper wheel rotating at a surface speed of 26 m/s
under Ar atmosphere. The ribbons were then crushed into
powder with a size of 150–200 lm. The starting ribbons
were well blended with pure Zn powder (0–2 wt. %) in the
glove box. Then, the mixture was put into the tungsten car-
bide mold, and then hot-pressed in the vacuum hot-press fur-
nace at a temperature of 700 �C for 2 min. The compressive
stress was 450 MPa. Hot-deformed magnets were prepared
by hot deforming the hot-pressed samples at about
800–850 �C with a pressure of 40–60 MPa. The hot deforma-
tion rate was 0.03 mm/s. The specimens were treated by nu-
merical control wire cutting and the magnetic properties of
magnets were measured by vibrating sample magnetometer.
The structure and microstructure of hot-deformed magnets
were examined by X-ray diffraction (XRD) with a Cu-Karadiation and transmission electron microscopy (TEM),
respectively.
Fig. 1 shows the magnetic properties of HD
(NdDy)11.5Fe81.5�xNbxB6 (x¼ 0–2) with different Zn addi-
tion. For HD magnets with Zn-free, the magnetic properties
increase largely with increasing Nb content. The enhanced
performance results from the formation of the c-axis texture
of Nd2Fe14B. As shown in Figs. 2(a) and 2(e), the c-axis tex-
ture is developed after 2% Nb addition, since the intensity of
(00 l) peaks and peaks with direction close to (00 l), such as
(006) and (105) peaks, increase largely. For the mechanism
of performance enhancement by Nb addition, Li et al. have
pointed out that Nb can be enriched at the amorphous graina)Electronic mail: [email protected]
0021-8979/2014/115(17)/17A704/3/$30.00 VC 2014 AIP Publishing LLC115, 17A704-1
JOURNAL OF APPLIED PHYSICS 115, 17A704 (2014)
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boundary, which can improve the grain refinement and pro-
mote the c-axis texture formation during hot-deformation,
thus leading to the better magnetic properties.15
For HD magnets with 1% Nb, the magnetic properties
increase largely with Zn content increasing from 0 to 2 wt.
%, and Hci and (BH)m increase from 146 kA/m and 51 kJ/m3
to 670 kA/m and 175 kJ/m3, respectively, according to Fig.
1. From Figs. 2(c) and 2(d), it can be seen that the c-axis tex-
ture is improved greatly after 2 wt. % Zn addition. The
enhancement of magnetic properties can be ascribed to the
developed c-axis texture and improved microstructure by Zn
addition, which has been discussed in detail at our previous
papers.13,14
However, the magnetic properties of HD magnets with
different Nb content display very different variation trends
with increasing Zn addition as shown in Fig. 1. For HD mag-
nets with Nb-free, the magnetic properties increase little
with increasing Zn from 0 to 2 wt. %, and Hci increases from
97 kA/m to 130 kA/m and (BH)m increases from 24 kJ/m3 to
38 kJ/m3. On the other hand, (BH)m reaches its maximal
value at Zn content of 1 wt. % and is 165 kJ/m3 for HD mag-
nets with 2% Nb. When Zn content increases to 2 wt. %, Br
and (BH)m decrease to 0.99 T and 127 kJ/m3.
The magnetic properties are intimately related to the
microstructure evolution. Fig. 3 shows the TEM micrographs
of HD magnets with different additions. As shown in Fig. 3,
the microstructure of hot-pressed (NdDy)11.5Fe82.5B6 alloys
with 2 wt. % Zn addition consists of uniform and equiaxial
grains with size of about 60 nm. However, the HD magnets,
with a poor c-axis texture according to Fig. 2(b), have a very
inhomogeneous microstructure and grain size is more than
150 nm, which leads to poor magnetic properties since Br
and Hci of nanocomposite magnets are sensitive to the grain
size. For HD (NdDy)11.5Fe80.5Nb2B6 with 1 wt. % Zn, the
grains are elongated and aligned on the whole normal to the
press direction and platelet-shaped with thickness of about
100 nm and length of more than 300 nm. At the same time,
the c-axis texture is well developed according to the XRD
pattern in Fig. 2(f), since peaks of (105) and (006) become
the strongest peaks. The uniform microstructure and strong
c-axis texture can lead to improved magnetic properties.
Thus, the good Br and Hci values can be obtained.
Our previous studies have shown that the addition of Zn
can improve markedly the texture formation and magnetic
properties of HD nanocomposite Nd-Fe-Nb-B magnets.13,14
The improvement mechanism was considered to be that Zn
can diffuse easily during hot-pressing and hot-deformation
and be enriched at amorphous grain-boundaries, which is
helpful to the growth of oriented Nd2Fe14B grains and
increase the decoupling effect between Nd2Fe14B grains.
However, that does not answer why the Zn addition cannot
improve the microstructure and magnetic properties of HD
Nd-Fe-B magnets without Nb. For HD Nd-Fe-B alloys, the
Nd-rich intergranular phase is believed to be critical to the
c-axis texture formation, which has a low melting-point and
can provide a mass transport pass for growth of favorably
oriented Nd2Fe14B grains during hot-deformation.4,5
FIG. 1. Magnetic properties of HD (NdDy)11.5Fe82.5�xNbxB6 (x¼ 0� 2)
with different Zn addition.
FIG. 2. XRD patterns of HD (NdDy)11.5Fe82.5�xNbxB6 (x¼ 0� 2) with dif-
ferent Zn addition (y¼ 0� 2 wt. %): (a) x¼ 0, y¼ 0; (b) x¼ 0, y¼ 2; (c)
x¼ 1, y¼ 0; (d) x¼ 1, y¼ 2; (e) x¼ 2, y¼ 0; (f) x¼ 2, y¼ 1; and (g) x¼ 2,
y¼ 2.
17A704-2 Ma et al. J. Appl. Phys. 115, 17A704 (2014)
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According to Fig. 2(a), the (NdDy)11.5Fe82.5B6 alloy consists
of two phases, Nd2Fe14B and a spot of a-Fe. Since nanocom-
posite Nd2Fe14B/a-Fe alloys contain little Nd-rich intergra-
nular phase, the fine equiaxed-grains in the hot-pressed
alloy grow randomly during hot-deformation, leading to the
poor c-axis texture and magnetic properties of HD
(NdDy)11.5Fe82.5B6 alloy. Additionally, it is also difficult for
Zn to diffuse into the matrix particle during hot-pressing and
hot-deformation as the little amount of intergranular phase
which provides the fast-diffusion pass. Thus, Zn addition has
little effect on the microstructure and magnetic properties of
HD (NdDy)11.5Fe82.5B6 alloy.
With increasing Nb content, as shown in Fig. 1, the rem-
anence and coercivity of HD alloys increase largely and are
further improved by Zn addition. However, the effect of Zn
addition is very different with increasing Nb. With increas-
ing Zn addition, HD (NdDy)11.5Fe81.5Nb1B6 alloy has good
magnetic properties at the Zn content of 2 wt. %, but HD
(NdDy)11.5Fe80.5Nb2B6 alloy reaches its maximal (BH)m
when the content of Zn addition is only 1 wt. %. For nano-
composite Nd2Fe14B/a-Fe alloys, Nb addition can enhance
the formation of amorphous grain boundary.15 On the one
hand, it can also improve the grain refinement and texture
formation during hot-deformation, thus the magnetic proper-
ties of HD alloys increase with increasing Nb content.
On the other hand, the amorphous intergranular phase can
provide the fast-diffusion pass for Zn atoms during
hot-working, and Zn is enriched at the grain boundary after
hot-deformation, which can further improve the texture for-
mation and coercivity. Thus, with increasing Nb content, the
volume fraction of intergranular phase increases and more
Zn can be enriched at grain boundaries. However, Zn can
react with Nd2Fe14B and resulting in the formation of other
phases such as a-Fe, Nd-Zn, and Fe-Zn during hot-working,
which decrease the content of hard magnetic phase.13 When
Nb content is up to 2%, more Zn can diffuse into the inter-
granular phase, leading to the introduction of more
non-magnetic phases. From the XRD pattern shown in Fig.
2(g), it can be seen the content of a-Fe in the HD
(NdDy)11.5Fe80.5Nb2B6 with 2 wt. % Zn is higher than
that without Zn. Thus, the magnetic properties of HD
(NdDy)11.5Fe80.5Nb2B6 magnets decrease after the addition
of 2 wt. % Zn due to the introducing of too much
non-magnetic phases.
Additionally, we found the coercivity of HD
(NdDy)11.5Fe81.5Nb1B6 with 2 wt. % Zn has a special varia-
tion tendency. It increases up to 22% first, and then decreases
gradually with increasing deformation. This may result from
that the grain boundary diffusion of Zn can lead to the
enhancement of magnetic decoupling effect between
Nd2Fe14B grains, which may be dominant in the early stage
of hot-deformation.
In summary, a way for improving the HD nanocom-
posite Nd2Fe14B/a-Fe magnets has been provided by com-
bining Nb and Zn additions. The magnetic properties and
microstructure can be only improved in that alloys with
Nb by Zn diffusion along the grain boundary. With
increasing Nb content to 2%, the maximal value of (BH)m
of 165 kJ/m3 was obtained by less Zn addition, resulting
from the good microstructure and strong c-axis texture.
Additionally, the coercivity of HD (NdDy)11.5Fe81.5Nb1B6
with Zn addition increased first with increasing deforma-
tion due to the further diffusion of Zn into the grain
boundary.
This work was supported by the National Natural
Science Foundation of China (No. 51201191), the Research
Foundation of Chongqing Education Committee (No.
KJ121415), and the Chongqing Natural Science Foundation
(No. CSTC2012JJA50004).
1E. F. Kneller and R. Hawig, IEEE Trans. Magn. 27, 3588 (1991).2D. Lee et al., IEEE Trans. Magn. 39, 2947 (2003).3R. K. Mishra, J. Appl. Phys. 62, 967 (1987).4L. Li and C. D. Graham, Jr., IEEE Trans. Magn. 28, 2130 (1992).5H. W. Kwon et al., IEEE Trans. Magn. 45, 2590 (2009).6Y. L. Huang et al., J. Appl. Phys. 111, 033913 (2012).7H. W. Kwon and G. C. Hadjipanayis, J. Magn. Magn. Mater. 310, 2575
(2007).8D. Lee et al., J. Appl. Phys. 99, 08B516 (2006).9Y. G. Liu et al., Appl. Phys. Lett. 94, 172502 (2009).
10A. M. Gabay et al., J. Magn. Magn. Mater. 302, 244 (2006).11D. Lee et al., IEEE Trans. Magn. 40, 2904 (2004).12X. Tang et al., Appl. Phys. Lett. 102, 072409 (2013).13Y. L. Ma et al., J. Magn. Magn. Mater. 322, 2419 (2010).14Y. L. Ma et al., IEEE Trans. Magn. 45, 2605 (2009).15J. Li, Y. Liu, and Y. L. Ma, J. Magn. Magn. Mater. 324, 2292 (2012).
FIG. 3. TEM of hot-pressed (a) and hot-
deformed (b) (NdDy)11.5Fe82.5B6 with
2 wt. % Zn addition and hot-deformed
(c) (NdDy)11.5Fe80.5Nb2B6 magnets
with 1 wt. % Zn addition.
17A704-3 Ma et al. J. Appl. Phys. 115, 17A704 (2014)
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