40 to 95 (wt% Fe) as Figure 2 shown. The preferred orientations are (111) and (200) reflections for fcc phase and (110) reflection for bcc phase. The (200) peak degrades with the increase of iron content. The results are in agreement with those of Ni-Fe alloys obtained in a rotating cylindrical electrode . The data indicate that the as-deposited Ni-Fe alloys are metastable.
The Ni-Fe alloy grain size obtained from XRD data is comparative with those results of TEM [13,15]. In the present study, the grain size was analyzed using the XRD line broadening analysis of the (111) peak for fcc Ni-Fe alloys and the (110) peak for bcc Ni-Fe alloys by means of the MDI Jade 5.0 software. The grain sizes of Ni-Fe alloys with 30%, 40%, 55%, 65% and 73% iron were 9.7, 8, 4.7, 5.6 and 12.1 nm, respectively. For pure fcc Ni-Fe alloys, the grain size decreased with the increase of iron content. This result is in good agreement with that of Ni-Fe alloys prepared in other baths . Over 55% iron, the grain size, however, increased with the increase of iron content. This grain size reversal may be due to the formation of bcc phase.
3.2. Thermal Stability of Ni-Fe Alloy Foils
As we know, saccharin, a typical organo-sulfur compound, can refine grain size of deposits but induce the sulfur impurity into nickel  or Ni-Fe alloy deposits . It was considered that the sulfur impurity resulted in the thermal embrittlement of deposits [21,22]. Dini et al.  indicated that the low-melting-point Ni-NiS2 formed in the grain boundaries, thus destroying cohesion between grains as the temperature increased. Sulfur segregation in the grain boundaries had also been detected in Ni and Ni-Fe alloys by Hibbard . Some researchers added Mn  and Re  into the Ni bath to co-deposit with Ni, and these Ni-Mn and Ni-Re alloys prevent the
Figure 1.X-ray diffraction patterns of as-deposited Ni-Fe alloys with different iron contents.
Figure 2. The Fe-Ni phase diagram from a literature .
Table 1 shows the ductility of the Ni-Fe alloys annealed at different temperatures. All as-deposited Ni-Fe alloys exhibit ductile. For all Ni-Fe alloys, it can be seen that a ductile-brittle-ductile transformation process ˚C occurred when the annealing temperature increased.
It was found from Table 1 that the embrittlement region became narrower when iron content increases, implying that Fe also inhibits the sulfur embrittlement.
But these Ni-Fe alloys did not exhibit an embrittlement property any more, after they were annealed at a high temperature (for example 650˚C), indicating that the ductile-brittle-ductile transformation is irreversible. Views of ductile and brittle Ni-65% Fe alloy foils annealed respectively at 650˚C and 200˚C were shown in Figure 3.
Figure 4 shows XRD patterns of the Ni70Fe30 alloy annealed at different temperatures. The strongest diffraction peak of (111) rapidly became high along with the annealing temperature, implying a growth of alloy grains. For example, at 200˚C the grain of this alloy grew from
Table 1. Ductility* of the Ni-Fe alloys annealed at different temperatures.
Figure 3. Views of (a) ductile and (b) brittler Ni-Fe alloy foils.
Figure 4. X-ray diffraction patterns for the Ni-30% Fe alloy annealed at temperatures.
9.7 to 12 nm calculated by the MDI Jade 5.0 software. However, a rapid grain growth took place at 300˚C, this temperature corresponds closely with that of electrodeposited Ni-Fe alloys reported elsewhere [13,18,19]. Additionally, as expected in Figure 2 the annealing did not lead to phase change.
It can be observed from Figure 4 that the (111) diffraction peak showed right-left-right shift along with the increase of annealing temperature. At low temperatures (<300˚C) sulfur should segregate to grain boundaries, resulting in brittleness transformation [21,22,25]. Thuvander  considered that rather than being caused by diffusion the observed sulphur segregation in nanocrystalline nickel may be a drag effect of moving grain boundaries. Hence, the (111) peak hardly shift.
At high temperatures (for example 500˚C), segregated sulfur gets dissolved interstitially into the bulk lattice, which leads to an increase in lattice constant, and concomitantly to a decrease (i.e. a shift to the left) in diffraction angle. It cannot, however, explain the shift to higher Bragg angles (the right) at 650˚C. At the temperature, irreversible brittle-ductile transformation in the Ni-Fe alloys occurred and was affected by Fe content in these alloys. The results indicated that the Sulfur might disappear from the bulk lattice by formation of sulfide precipitate contained Fe.
The evolution of XRD patterns of Ni60Fe40 is similar to the Ni70Fe30 alloy, and consequently the data were not shown here.
Figure 5 shows XRD patterns of the Ni45Fe55 alloy annealed at different temperatures. At 300˚C, the alloy exhibited also a rapid grain growth, and presented mixed phases with fcc (a main phase) and bcc, according with the Fe-Ni equilibrium phase diagram (Figure 2). When Ni-Fe alloys are annealed at higher than the γ-(Fe, Ni) phase boundary temperature (about 428˚C for the Ni45Fe55 alloy), the bcc phase is hardly observed in the Figure 5, although there is a driving force for the formation of Fe rich bcc phase during the cooling process. The reason is likely that the formation of bcc phase is under kinetic control. Dokania et al.  demonstrated the bcc to fcc phase transition for Invar by short pulse laser treatment, and found that the fcc phase became gradually a main phase with increasing the pulse times. This indicated that the role of heat treatment is the same as that of laser treatment.
Although the as-deposited alloys exhibited a different phase, namely bcc, the evolutions of XRD patterns of the Ni35Fe65 and Ni27Fe73 alloys (see Figure 6) are similar to that of the Ni45Fe55 alloy. It can be seen that at 300˚C the fcc phase is still a main phase, indicating that its formation is under thermodynamic control. For the Ni27Fe73 alloy, a difference was that diffraction peaks shift to right
Figure 5.X-ray diffraction patterns for the Ni-55% Fe alloy annealed at temperatures.
2θ (deg) 2θ (deg)
Figure 6. X-ray diffraction patterns for the (a) 65% Fe-Ni alloy and (b) 73% Fe-Ni alloy annealed at different temperatures.
occurred at 500˚C, when the alloy became ductile.
3.3. Representative Tensile Curves
Figure 7 shows the stress-strain curves of the Ni-65% Fe alloy as-deposited and annealed at 650˚C. The tensile strength is 995 MPa and 852 MPa for as-deposited and annealed at 650˚C, respectively. Different with the results of bend tests, these curves suggest the alloy as-deposited and annealed does not exhibit ductility. But the reason is unclear. However, four factors could affect the stressstrain curves: grain size, strain state, defects and thickness of these materials. For example, Li  demonstrated ductile-to-brittle transition in nanocrystalline metals by reducing grain size to their critical size (12 nm for the Ni-15% Fe alloy). Another example, Gu  found ductile-brittle-ductile transition in an electrodeposited 13 nanometer grain sized Ni-8.6 wt% Co alloy through increasing the strain rates from 1.04 × 10−5 to 1.04 s−1.
The phase of Ni100–xFex alloys in the as-deposited state is dependent on the iron content. A pure fcc phase is presented at low iron content (x < 55), a pure bcc phase at high iron content (x > 73), and fcc and bcc mixed phases
Figure 7. Stress–strain curves for electrodeposited Ni-65%Fe alloy (a) as-deposited and (b) annealed at 650˚C.
at middle iron content (55 < x < 73).
The ductile-brittle-ductile transformation occurred when Ni100–xFex alloys were annealed from room temperature to 650˚C. The embrittlement phenomenon arose from the sulfur segregation in grain boundaries. For Ni100–xFex alloys annealed at 200˚C, the ductility increased with the increase of iron content, indicating that iron can partly prevent the sulfur embrittlement, i.e. iron can improve thermal stability of Ni-Fe alloys. But nanocrystalline Ni-Fe alloys contained S impurity should be utilized only at a temperature of below 200˚C. Bcc to fcc phase transformation in the Ni100–xFex alloys (x > 55) was observed at the annealed temperature of over 300˚C.
This work was supported by Open Research Fund Program of Key Laboratory of Ethnic Medicine Resource Chemistry, State Ethnic Affairs Commission & Ministry of Education, Yunnan University of Nationalities, P.R. China (Fund Number: YMY1113), and supported by Program for Innovative Research Team (in Science and Technology) in University of Yunnan Province (IRTSTYN) and Green Chemistry and Functional Materials Research for Yunnan Innovation Team (2011HC008).