Effect of Cross-Rolling on Microstructure, Texture and Magnetic Properties of Non-Oriented Electrical Steels

Abstract

Hot rolled non-oriented electrical steel samples were subjected to cold cross-rolling of 80 % reduction in thickness. The cross-rolled samples were then annealed at 650, 750 and 850 ºC for 1 hr, 2 hrs and 4 hrs respectively. The role of cross-rolling on microstructure, texture and magnetic properties of the samples after annealing has been investigated. Two different samples were used for the present investigation - one had higher Al content (sample S1) while the other had higher C, Si, Mn, P and S content (sample S2). It was observed that the sample S1 had higher grain size compared to sample S2 after annealing. The cross-rolling was observed to be controlled the texture developments in the samples and it was found that the texture factor was identical in all directions of the sample. The core losses in the samples were found to be decreased with increasing grain size of the samples.

Keywords:
Electrical Steels; Cross-Rolling; Annealing; Texture; Core Loss

1. Introduction

Non-oriented electrical steels are widely used in electrical generators and motors where the magnetic field is important in all directions^1-3. To achieve adequate magnetic properties in all directions, both grain size and texture have been controlled through different thermo-mechanical processing of these steels^4-7. An optimum grain size is essential for minimum watt loss in the material - for example, the optimum grain sizes are 100 and 150 micron for 1.85 and 3.2 % Si steels respectively⁸. Texture components like (001)<uvw> and (111)<uvw> are considered respectively as good and bad texture components from magnetic properties point of view^9,10. However, various texture components other than (001) <uvw> texture of these steels i.e. goss {110} <100>, cube {100} <001> and eta {hkl} <100> are also good texture components from magnetic properties viewpoint¹¹. At present no method is feasible for the production of (001)<uvw> texture in all directions. Therefore, in the entire world isotropic non-oriented steels with multi-component texture have been developed for this purpose. Multistep cross-rolling (MSCR) has been observed to be an efficient method to randomize the texture of a material^12-15. During MSCR, the material is rotated by 90º in the intermittent steps of the rolling¹⁶. In the present study the effect of MSCR processing and subsequent annealing of hot rolled non-oriented electrical steels on microstructure, texture and magnetic properties of these steels have been investigated.

2. Experimental Details

2.1. Material and Sample Preparation

Hot rolled steels of 2.3 mm thickness were used as the starting material for the present study. Two different samples were used for the present investigation - sample S1, had higher Al content and sample S2 which had higher C, Si, Mn, P and S content. The chemical composition (in wt.%) of the samples is shown in Table 1. The steels were subjected to multi-step cross-rolling (MSCR) in a laboratory rolling mill down to 80 % reduction in thickness. During each steps of MSCR, true strain was maintained at 10 %. The MSCR samples were subjected to annealing at 650, 750 and 850 ºC for 1 hr, 2 hrs and 4 hrs respectively. The samples were then metallographically polished for subsequent characterizations.

Table 1
Chemical composition (in wt.%) of steel samples used in the present study. The balance amount was being Fe.

Sample	C	Si	Mn	P	S	Al	Cr	Mo	Ni	Cu
S1	0.0376	1.45	0.305	0.0201	0.018	0.0965	0.007	0.0021	0.0097	0.012
S2	0.0390	1.52	0.350	0.0216	0.020	0.0525	-	-	-	-

2.2. Optical Microscopy

Optical microstructures of the samples were characterized using a Zeiss AxioCam ERc 5s image analyzer. The samples were etched with nital solution for the microstructural analysis.

2.3. X-Ray Diffraction (XRD)

XRD was carried out in a Bruker D8-Advance system using Co K_α radiation. Three pole figures, (110), (200) and (211), were measured on the ND plane containing the RD-TD direction. RD corresponds to the rolling direction whereas ND and TD correspond to the normal and transverse direction respectively. Orientation distribution functions (ODFs) were calculated using the Labotex 3.0 software¹⁷. Using the software, volume fractions of different texture components were estimated through integration method with a 15° tolerance on the deviation from the ideal orientation(s).

2.4 Magnetic Measurements

Magnetic measurements were carried out on Brockhaus MPG 200 instrument. The core losses at 1.5 T and 50 Hz were obtained along RD of the samples. The samples were measured on single sheet tester of size 210 mm × 210 mm. For one condition three samples were measured in order to get the accuracy of the measurement.

3. Results

Figures 1 and 2 respectively show the optical microstructures of sample S1 and sample S2 at different conditions of annealing. A near equiaxed grains were observed in both the samples. However, a distinct bimodal distribution of grains was observed during annealing of the sample S1 at lower temperature (650º C) and at higher temperature of annealing, it had abnormal grain growth. A regular increase in grain size as a function of both annealing temperature and annealing time was observed in the samples after annealing. Figure 3 shows the average grain size of the samples at different annealing conditions. The rate of grain growth was relatively higher when annealed at 850 ºC. Also the sample S1 had higher grain size than that of sample S2 after annealing.

Figure 1
Optical microstructures of the sample S1 at different annealing conditions.

Figure 2
Optical microstructures of the sample S2 at different annealing conditions.

Figure 3
Average grain size of the samples as a function of temperature and time of annealing: (a) sample S1 and (b) sample S2.

Figures 4 and 5 respectively show the ODFs, at constant φ₂ = 45º, of samples S1 and S2 at different conditions of annealing. It may be observed that the γ-fiber was distinct in sample S2. However, in sample S1 the fiber was not clear except during annealing at 650 ºC, and at 850 ºC for 2 hrs of annealing time. The volume fraction of texture factor i.e. (111)<uvw>/(001)<uvw> ¹⁰ as a function of annealing temperature and time in samples S1 and S2 are shown in Figure 6. The following observations may be obtained from Figure 6:

Figure 4
ODFs, at constant φ₂ = 45º, of sample S1 at different annealing conditions.

Figure 5
ODFs, at constant φ₂ = 45º, of sample S2 at different annealing conditions.

Figure 6
Volume fraction of texture factor i.e. (111)<uvw>/(001)<uvw> as a function of annealing time at different temperatures of annealing for: (a) sample S1 and (b) sample S2.

• At 650 ºC annealing temperature: The texture factor decreased, though not significantly, as a function of annealing time for sample S1. Whereas in case of sample S2, it was increased till 2 hrs of annealing time and the decreased on further increasing the annealing time of 4 hrs.

• At 750 ºC annealing temperature: For sample S1, the texture factor was decreased till 2 hrs of annealing time and then increased at 4 hrs of annealing time. However, the texture factor was decreased with increasing annealing time may be observed in sample S2.

• At 850 ºC annealing temperature: An increased texture factor with increased annealing time was observed in sample S1. However, in sample S2 the texture factor was initially decreased till 2 hrs of annealing time and then increased on further increasing the annealing time of 4 hrs.

As shown in Table 2, it can be observed that the texture factor along all other directions were approximately similar to the values observed along RD.

Table 2
Texture factor of the samples as a function of sample orientation.

Annealing Condition	Texture Factor at different sample orientation (w.r.t the rolling direction)
	Sample S1									Sample S2
Temp. (ºC)	Time (hrs)	0º	45º	90º	135º	180º	225º	270º	315º	0º	45º	90º	135º	180º	225º	270º	315º
650	1	1.63	1.62	1.64	1.62	1.64	1.62	1.65	1.63	0.98	0.96	0.97	0.98	0.97	0.97	0.97	0.96
	2	1.61	1.61	1.57	1.60	1.61	1.55	1.61	1.55	2.12	2.11	2.11	2.11	2.14	2.10	2.11	2.12
	4	1.47	1.47	1.47	1.48	1.47	1.47	1.48	1.47	1.50	1.50	1.48	1.48	1.48	1.49	1.49	1.48
750	1	1.41	1.29	1.31	1.32	1.32	1.33	1.32	1.27	1.33	1.32	1.32	1.34	1.32	1.32	1.32	1.32
	2	1.30	1.31	1.30	1.31	1.30	1.31	1.31	1.30	1.20	1.18	1.19	1.18	1.20	1.19	1.19	1.19
	4	1.52	1.52	1.49	1.46	1.53	1.47	1.50	1.49	1.18	1.17	1.16	1.16	1.17	1.17	1.15	1.16
850	1	1.01	1.01	1.00	1.01	1.01	1.01	1.01	1.02	1.71	1.69	1.68	1.70	1.68	1.70	1.69	1.68
	2	1.69	1.66	1.67	1.70	1.70	1.65	1.68	1.68	1.62	1.69	1.65	1.70	1.65	1.72	1.64	1.72
	4	1.72	1.72	1.70	1.72	1.71	1.71	1.71	1.70	1.76	1.74	1.74	1.76	1.72	1.71	1.74	1.76

Figure 7 shows the core losses of the samples at different annealing conditions. It was observed that the core losses were decreased with increasing the time of annealing. Also the sample S1 had relatively lower core losses compared to that of sample S2.

Figure 7
Core losses as a function of annealing temperature and annealing time for: (a) sample S1 and (b) sample S2. The core loss of the sample S1 before annealing was 12.17 W/kg and that of sample S2 before annealing was 14.183 W/kg.

4. Discussion

The magnetic properties of electrical steels largely depend on the chemical composition, crystallographic texture and grain size^4,10,18. The elements such as P, Si, Al and Mn are generally added to the steels to improve the resistivity^9,10,18. The other major elements such as C and S affect the magnetic properties of the steels and these contents should be lower for better magnetic properties of the steels. It has also been reported that the harmful effects of C and S can be minimized through second phase precipitation^5,19. The alloying elements also help in controlling the texture of the electrical steels through growth inhibition¹⁸. Mn is a good example of generating growth inhibitors during annealing of non-oriented electrical steels¹⁸. This might be the reason for the sample S2 to have lower grain size compared to sample S1 after annealing. Also it was observed that the abnormality in grain growth was seen in sample S1 (Figure 1) although sample S1 higher Al content which also can generate growth inhibitors⁵. However, Al has been observed to be detrimental to the workability of the samples and this could affect the stored energy of the sample during cold rolling which affects the subsequent grain growth of the sample.

Controlling the crystallographic texture and grain size of these steels mostly depends on the thermo-mechanical processing steps during the production. It has been found that an optimum grain size and low texture factor, (111)<uvw>/(001)<uvw>, is required for better magnetic properties of electrical steels¹⁰. However, unlike CRGO (cold rolled grain oriented) electrical steels where ideal texture is required along one direction/orientation, CRNO (cold rolled non-oriented) electrical steels the ideal texture is required in all direction. The present study is an attempt to weaken/randomize the texture of the steels rather than improving the ideal texture in all directions. Cross-rolling has been a successful method to weaken the texture of cubic metals^12-15. This was also observed in the present study which showed that the texture factor was identical in all directions of the samples (Table 2). The possible explanation for the formation of suitable recrystallization textures can be attributed to a combination of oriented nucleation and oriented growth, deformation accumulated stored energy, geometric softening and orientation pinning^18,20,21. In the present study, however, the mechanism of recrystallization texture development is not debatable as the texture factor in the samples was not very different (Figure 6, Table 2). The significant increase in texture factor of sample S1 annealed at 850 ºC for 2 - 4 hrs of annealing time (Figure 6a) may be attributed to the oriented growth mechanism (Figure 1). However, the increase in texture factor of sample S2 annealed at 650 ºC for 2 hrs of annealing time (Figure 6b) could be attributed to the combination of different recrystallization texture mechanisms²¹.

The magnetic property of the samples, represented by core losses, was found to be dependent mainly on the average grain size of the samples although texture factor was also important (Figures 3, 6 and 7). The higher the grain size of the sample lowered the core losses in the sample. It also indicated that the abnormality in grain growth in the sample S1 was not detrimental from the magnetic property viewpoint.

5. Summary

In the present study, the effect of chemistry and cross-rolling on the microstructure, texture and magnetic properties of non-oriented electrical steels have been investigated. It was found that the electrical steel sample with higher Mn content showed normal grain growth whereas the sample with higher Al content showed abnormal grain growth during annealing of the samples. The cross-rolling prior to annealing of the samples had a significant effect on the texture developments in the samples and the samples had similar texture factor in all directions of the samples. It was also observed that the samples with higher grain size had lower core losses.

6. Acknowledgement

The authors would like to thank Prof. S. Suwas of IISc Bangalore for conducting rolling of the samples in his laboratory.

7. References

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Publication Dates

• Publication in this collection
  16 Dec 2016
• Date of issue
  Jan-Feb 2017

History

• Received
  09 June 2016
• Reviewed
  11 Oct 2016
• Accepted
  21 Nov 2016