CN1183269C - Non-oriented electromagnetic steel sheet and method for producing therefor - Google Patents

Non-oriented electromagnetic steel sheet and method for producing therefor Download PDF

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CN1183269C
CN1183269C CNB018014402A CN01801440A CN1183269C CN 1183269 C CN1183269 C CN 1183269C CN B018014402 A CNB018014402 A CN B018014402A CN 01801440 A CN01801440 A CN 01801440A CN 1183269 C CN1183269 C CN 1183269C
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steel
steel sheet
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oriented electromagnetic
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CN1380908A (en
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尾田善彦
彦
寒川孝
明
日裹昭
田中靖
小野義彦
占部俊明
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JFE Engineering Corp
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NKK Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

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Abstract

A non-oriented electromagnetic steel sheet having a chemical composition in mass %: C: 0.005 % or less, Si: 1.5 to 3 %, Mn: 0.05 to 1.5 %, P: 0.05 % or less, S: 0.02 % or less, Al: 0.1 to 2 %, N: 0.005 % or less, Cr: 0.4 to 1.4 %, and balance: substantially Fe; a non-oriented electromagnetic steel sheet having a chemical composition in mass %: C: 0.005 % or less, Si: 4 % or less, Mn: 0.05 to 2 %, P: 0.1 % or less, S: 0.02 % or less, Al: 0.1 to 2 %, N: 0.005 % or less, Cr: 0.4 to 5 %, Ti: an amount satisfying Ti/C = 1 to 30, and balance: substantially Fe, provided that Mn / S >/= 10; a non-oriented electromagnetic steel sheet having a chemical composition in mass %: C: 0.01 % or less, Si: 1 to 4 %, Mn: 1 % or less, P: 0.05 % or less, S: 0.02 % or less, Al: 0.1 to 2 %, N: 0.005 % or less, Cr: 0.2 to 5 %, at least one of 0.05 to 0.5 % Cu, 0.002 to 0.1 % Sb and 0.002 to 0.1 % Sn, and balance: substantially Fe; and other two types of non-oriented electromagnetic steel sheet. Such non-oriented electromagnetic steel sheets are excellent in blanking characteristics and fatigue characteristics and are reduced in iron loss both before and after stress relieving annealing, and thus are very suitable as an iron core material of a motor for an electric car and an air conditioner and the like.

Description

Non-oriented electromagnetic steel sheet and manufacture method thereof
Technical field
The present invention relates to have good pressworkability and fatigue property, the frequency non-oriented electromagnetic steel sheet that iron loss is low after the stress relieving below the 1000Hz and manufacture method thereof.
Background technology
From the viewpoint of electric appliance energy-saving, the core material that electrical equipment uses requires to adopt the lower non-oriented electromagnetic steel sheet of iron loss in recent years.Generally, in order to reduce the iron loss of electrical sheet, utilize the content that increases Si and Al, the resistivity that increases it is effective, for example the spy opens to disclose in the clear 53-66816 communique and uses the steel that contains Si:1.6-3.5%, Al:0.2-2.5%, by twice cold rolling repeatedly and annealed secondary cold-rolling method, to reduce the method for iron loss.Special public clear 56-22931 communique disclose by the composition of steel is adjusted into Si:2.6-3.5%, Al:0.3-1.0%, below the S:0.0050%, below the O:0.0025%, Te Kaiping 5-140647 communique disclose by the composition of steel is adjusted into Si:2.0-4.0%, Al:0.10-2.0%, below the S:0.0030%, Ti, Zr, Nb, V: respectively below 0.0050%, to reduce the method for iron loss.
On the other hand, from the miniaturization of used for electric vehicle motor and idle call motor and the viewpoint of raising the efficiency, the frequency of these motors is developed to the high frequency direction of 200-1000Hz, require the non-oriented electromagnetic steel sheet of the iron core use of motor, even iron loss is low under high like this frequency.Be effective more than the Si:4% for this reason, but owing to steel plate will become fragile, so nearest spy opens flat 11-229095 communique and Te Kai 2000-119822 communique proposes not exist the embrittlement problem, that iron loss is low, as to contain the high-Cr of Cr:0.5-5.5% and 1-8% non-oriented electromagnetic steel sheet.
Si and Al content are increased, or increase Cr content, the obvious hardening of steel plate is so easy mold damage during punch process just produces the problem that pressworkability worsens.
On the other hand, follow the variable-speed operation of motor, be added in its epitrochanterian centrifugal force and also become greatly, good fatigue property will be arranged so be used for the electrical sheet of iron core.Improve fatigue property, making the steel plate hardening is effectively, but can produce the problem that above-mentioned pressworkability worsens with existing method, does not also have all good non-oriented electromagnetic steel sheet of pressworkability and fatigue property now.
The iron core of the air compressor motor of high-level efficiency air-conditioning and refrigerator etc. will stack after with the non-oriented electromagnetic steel sheet punch process and carry out stress relieving, so iron loss is low after requiring stress relieving.Even above-mentioned existing electrical sheet iron loss before stress relieving is low, but sometimes also may not be low after stress relieving.
Summary of the invention
The purpose of this invention is to provide have good pressworkability and fatigue property, low non-oriented electromagnetic steel sheet and the manufacture method thereof of iron loss before and after the stress relieving of frequency below 1000Hz.
Can achieve the above object with following non-oriented electromagnetic steel sheet.
Containing quality % is C:0.0016-0.0029%, Si:2.5-3.0%, Mn:0.14-0.20%, P:0.005-0.01%, S:0.001-0.002%, Al:1.0-1.5%, N:0.0012-0.0024%, Cr:0.4-5%, Mg:0.0001-0.005%, and all the other are the non-oriented electromagnetic steel sheet of Fe.This electrical sheet also is to have good especially fatigue property, shows low iron loss simultaneously under high frequency.
The invention still further relates to the manufacture method of non-oriented electromagnetic steel sheet, comprise operation: quality % is that C:0.005% is following containing, Si:2.48-2.52%, Al:0.98-1.02%, Mn:0.17-0.19%, P:0.010-0.1 10%, N:0.0014-0.0022%, S:0.0003-0.0007%, Cr:0.4-5%, and all the other make slab for the steel of Fe; Pickling after the above-mentioned slab hot rolling, be cold rolled to specific thickness then, carry out continuous annealing again; To the steel plate after the hot rolling or cold rolling after steel plate carry out carbonization treatment, make C content at 0.0003-0.0015%.
Description of drawings
Fig. 1 is the diagram of expression Cr content and iron loss W15/50, Vickers' hardness Hv relation.
Fig. 2 is the diagram of expression Hv and punching press number of times relation.
Fig. 3 is expression Si+0.5 * Al+0.2 * Cr and the (diagram of the relation of punching press number of times/W15/50).
Fig. 4 is the diagram of expression Cr content and iron loss W10/400 relation.
Fig. 5 is the diagram of expression Ti/C and safe range of stress relation.
Fig. 6 is for representing the diagram of Cr content and iron loss W10/600, magneticflux-density B50, Hv relation.
Fig. 7 is the diagram of expression Mg content and safe range of stress relation.
Fig. 8 is the diagram of expression Cu content and W10/400 relation.
Fig. 9 is the diagram of expression Sb content and W10/400 relation.
Figure 10 is the diagram of expression Sn content and W10/400 relation.
Figure 11 is the diagram of expression Cr content and W10/400 relation.
Figure 12 is the diagram of expression C content and W10/400 relation.
Figure 13 is the diagram of expression Cr content and W10/400 relation.
Embodiment
We have carried out detailed research to the iron loss before and after the stress relieving below 1000Hz of the pressworkability of non-oriented electromagnetic steel sheet, fatigue property, frequency, it found that, cooperate by adding Cr and other element proper content, can access the non-oriented electromagnetic steel sheet of the above-mentioned 1-5 that the iron loss before and after the stress relieving is all low under all good and high frequency of pressworkability and fatigue property.Be elaborated below.
The non-oriented electromagnetic steel sheet that embodiment 1. pressworkabilities are good
1) reason of determinant
C: in order to prevent that magnetic aging from making C content is being necessary below 0.005%.In order to suppress the rising to the disadvantageous hardness of pressworkability, preferred C content is below 0.0009% in addition.
Si: because the resistivity of steel plate is increased, thus be the effective element that reduces iron loss, if but surpass 3%, then cause hardness to raise, pressworkability worsens.Reduce Si content and can reduce hardness, favourable to improving pressworkability, but iron loss improves.Utilize in the present invention to add that Cr suppresses, and Si content is lower than the effect that 1.5% words do not have this inhibition owing to reduce the iron loss that Si content brings and increase.
Mn: if surpass 1.5%, then magneticflux-density reduces significantly.In order to prevent red brittleness, Mn content must be more than 0.05% in addition.
P: if surpass 0.05%, then hardness obviously improves, and pressworkability worsens.As described later, add Cr realization soft in order to effectively utilize, preferred P content is below 0.01%.
S: if surpass 0.02%, can separate out MnS, iron loss raises.Owing under the poor situation of Mn, have to cause hot short danger, preferred S content is below 0.0009%.
Al: identical with Si, be the element that increases steel plate resistivity, the words magneticflux-density above 2% reduces significantly.If be lower than 0.1%, separate out fine AlN entirely, hinder grain growth, cause high iron loss.
N:, cause iron loss to increase, so should be below 0.005% owing to separate out with the AlN form.
Cr: reason requires to be 0.4-1.4% as described later.
All the other: be essentially Fe.
2) Cr content and iron loss W15/50, Vickers' hardness Hv relation
The steel of smelting in testing laboratory contains C:0.0020%, Mn:0.10%, P:0.005%, S:0.002%, Al:1%, N:0.0021%, Cr content is changed between tr. (trace: be essentially 0%)-2.5%, for the resistivity that makes steel plate constant, adjust Si content, making Si+0.5Cr is 3%.Behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min.Measure the Hv of steel plate plate face and the average W15/50 that measures rolling direction and vertical rolling direction with Epstein iron loss assay method then.
As shown in Figure 1, W15/50 does not raise in Cr is the 0.4-1.4% scope as can be seen, and Hv reduces, and pressworkability is good.Cr content surpasses 1.4%, and the reason that Hv raises is thought because the avidity of Cr and N is big, forms one deck nitride layer at surface of steel plate.
Add that to add the following and Nb:0.005% of Ti:0.005% behind the above-mentioned element more at least a kind of in following, iron loss does not raise, and can reliably prevent magnetic aging.
3) relation of Hv and pressworkability
The steel of smelting in testing laboratory contains C:0.0025%, Mn:0.20%, P:0.01%, S:0.002%, Al:1%, N:0.0021%, Cr:1.0%, Ti:0.001%, make Si content in the 1.5-3.0% range, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, apply inorganic organic membrane then.The internal diameter of punching press repeatedly 70mm with 10%, the ring-shaped sample of external diameter 100mm, the punching press number of times that surpasses 50 μ m with burr height is estimated pressworkability.If because press tool wearing and tearing, the burr height of the material that is stamped will increase, so the many more material pressworkability of punching press number of times is good more.
As shown in Figure 2, make Hv below 190 as can be seen, the punching press number of times increases, and can access better pressworkability.
4) relation of Si+0.5 * Al+0.2 * Cr and punching press number of times/W15/50)
The steel of smelting in testing laboratory contains C:0.0020%, Mn:0.20%, P:0.01%, S:0.002%, N:0.0020%, Ti:0.001%, and the content of Si, Al, Cr is changed within the scope of the present invention, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, apply inorganic organic membrane then.Measure W15/50 and punching press number of times with aforesaid method.
Fig. 3 represents Si+0.5 * Al+0.2 * Cr and the (relation of punching press number of times/W15/50).Wherein Si+0.5 * Al+0.2 * Cr represents to consider the solution strengthening rate of each element weighting, and the big more hardness of this value is high more.In addition (equilibrium of the expression of punching press number of times/W15/50) W15/50 and pressworkability, it is good more that this is worth big more pressworkability, and W15/50 diminishes.Making Si+0.5 * Al+0.2 * Cr as can be seen is 2.3-3.5, and (value of punching press number of times/W15/50) is big, W15/50 and pressworkability balanced better.On the other hand, can access good pressworkability under less than 2.3 situation at Si+0.5 * Al+0.2 * Cr, but the W15/50 height.Si+0.5 * Al+0.2 * Cr surpasses 3.5, and W15/50 is low, and pressworkability worsens.
(embodiment 1)
With the processing that outgases of the molten steel of converter smelting, the steel 1-25 of composition shown in the melting table 1 is cast as slab, after heating under the 1140 ℃ * 1hr condition, carries out the hot-rolled steel sheet that thickness of slab 2.0mm is made in hot rolling.800 ℃ of final rolling temperatures, 610 ℃ of coiling temperatures during hot rolling.Hot-rolled steel sheet after batching is at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, apply inorganic organic membrane then.Measure Hv, magnetic (W15/50 and magneticflux-density B50), punching press number of times with aforesaid method.
The results are shown in table 1.
The W15/50 of steel 3-5 of the present invention, 8,15-18,20,22-23 is low, and pressworkability is good.
On the other hand, the comparative steel pressworkability is bad, or the W15/50 height.
Table 1
Steel C Si Mn P S Al N Cr Ti Nb Si+0.5Al+ 0.2Cr Hv Punching press number of times (* 10 4) W15/50 (W/kg) B50(T) Punching press number of times/(W15/50) (* 10 4) Remarks
1 0.0022 3.00 0.18 0.005 0.0020 1.00 0.0014 0.01 tr. tr. 3.50 210 50 1.95 1.66 26 Comparative example
2 0.0021 2.90 0.18 0.005 0.0020 1.00 0.0015 0.20 tr. tr. 3.44 206 60 1.96 1.66 31 Comparative example
3 0 0023 2.75 0.05 0 005 0.0020 1.00 0.0016 0.50 tr. tr. 3.35 189 145 1.94 1.66 75 Example
4 0.0029 2.53 0.17 0.005 0.0020 1.00 0.0024 0.95 tr. tr. 3.22 187 150 1.95 1.66 77 Example
5 0.0018 2.40 0.15 0.005 0.0020 1.00 0.0016 1.20 tr. tr. 3.14 186 155 1.96 1.65 79 Example
6 0.0018 2.10 0.15 0.005 0.0008 1.00 0.0015 1.80 tr. tr. 2.96 192 100 2.08 1.63 48 Comparative example
7 0.0016 1.75 0.15 0.005 0.0009 1.00 0.0015 2.50 tr. tr. 2.75 195 95 2.16 1.62 44 Comparative example
8 0 0035 2.53 0.15 0.010 0.0020 1.00 0.0028 0.95 0.0020 tr. 3.22 187 155 1.96 1.65 79 Example
9 0.0032 2.54 0.15 0.010 0.0020 1.00 0.0021 0.92 tr. 0.0020 3.22 187 160 1.97 1.65 81 Comparative example
10 0.0030 4.20 0.15 0.018 0.0020 tr. 0.0019 0.70 tr. tr. 4.34 230 30 1.95 1.63 15 Comparative example
11 0.0030 2.00 0.16 0.018 0.0020 2.50 0.0021 0.70 tr. tr. 3.39 190 130 2.01 1.60 65 Comparative example
12 0.0022 3.00 1.80 0.021 0.0020 0.27 0.0019 0.70 tr. tr. 3.28 185 130 2.08 1.62 63 Comparative example
13 0.0060 3.00 0.15 0.025 0.0020 0.26 0.0020 0.70 tr. tr. 3.27 195 90 2.63 1.63 34 Comparative example
14 0.0012 3.00 0.16 0.021 0.0020 0.27 0.0065 0.70 tr. tr. 3.28 195 95 2.85 1.63 33 Comparative example
15 0.0023 2.90 0.16 0.005 0.0020 0.80 0.0015 1.00 tr. tr. 3.50 190 150 2.00 1.67 75 Example
16 0.0020 2.40 0.16 0.005 0.0020 0.80 0.0017 1.00 tr. tr. 3.00 165 175 2.25 1.68 78 Example
17 0.0018 2.00 0.16 0.005 0.0020 0.80 0.0016 1.00 tr. tr. 2.60 145 180 2.40 1.70 75 Example
18 0.0018 1.60 0.16 0.005 0.0020 1.50 0.0016 1.00 tr. tr. 2.55 143 180 2.40 1.70 75 Example
19 0.0018 1.40 0.16 0.005 0.0020 1.30 0.0016 1.00 tr. tr. 2.25 128 190 3.20 1.70 59 Comparative example
20 0.0018 2.00 0.16 0.005 0.0020 0.80 0.0016 1.00 tr. tr. 2.60 145 180 2.40 1.70 75 Example
21 0.0029 3.20 0.17 0.005 0.0020 0.70 0.0024 0.20 tr. tr. 3.59 199 80 2.00 1.66 40 Comparative example
22 0.0018 3.00 0.17 0.005 0.0020 0.70 0.0020 0.40 tr. tr. 3.43 190 150 2.00 1.66 75 Example
23 0.0019 2.70 0.17 0.005 0.0020 0.70 0.0021 1.00 tr. tr. 3.25 178 160 2.05 1.65 78 Example
24 0.0019 2.35 0.17 0.005 0.0020 0.70 0.0021 1.70 tr. tr. 3.04 192 110 2.30 1.63 48 Comparative example
25 0.0019 2.90 0.17 0.005 0.0020 0.70 0.0021 0.20 tr. tr. 3.29 184 153 2.70 1.65 57 Comparative example
Embodiment 2. fatigue propertys are good, the low non-oriented electromagnetic steel sheet of iron loss under the high frequency
1). the reason of determinant
C: in order to prevent that magnetic aging requirement C content is below 0.005%.
Si: be the effective element that is used to increase the resistivity of steel plate, Si content surpasses 4% words magneticflux-density can be reduced significantly.
Mn: the words magneticflux-density above 2% can reduce significantly.In order to prevent that the red brittleness requirement will be more than 0.05%.
P: the words hardness above 0.1% obviously raises, and pressworkability worsens.
S: the words above 0.02% are separated out with the MnS form, and iron loss raises.
Al: identical with Si, be the effective element that is used to increase steel plate resistivity, but reduce significantly above 2% words magneticflux-density.Be lower than 0.1% words and can cause fine AlN to separate out, hinder grain growth, iron loss increases.
N: owing to separate out, iron loss is increased, so require below 0.005% with the AlN form.
Cr: reason as hereinafter described requires at 0.4-5%.
Reason as hereinafter described also contains Ti and Mn/S 〉=10 (containing the Ti steel) that Ti/C is 1-30, or Mg:0.0001-0.005% (containing the Mg steel).
All the other: be Fe basically.
2). contain the Ti steel
2-1) the relation of .Cr content and iron loss W10/400
The steel of smelting in testing laboratory contains C:0.0020%, Si:2.5%, Mn:0.18%, P:0.01%, S:0.002%, Al:0.7%, N:0.0011%, make Ti content be tr. and 0.008%, Cr content in the tr.-6% range, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 20%H 2-80%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, apply half organic membrane then, at 350 ℃ film is carried out sintering processes.For the driving condition of simulated machine carries out the thermal treatment of 200 ℃ * 100hr, once coil one side and secondary coil one side are measured the W10/400 under the 400Hz all around 100 circle leads on the ring-shaped sample of internal diameter 33mm, external diameter 45mm then.
As shown in Figure 4, Ti content is that steel W10/400 under the Cr:0.4-5% situation of 0.008% significantly diminishes as can be seen, particularly reduces significantly under the Cr:0.4-0.9% situation.Ti content is in the steel of tr. on the other hand, and the ratio that W10/400 reduces is little, and the trend of increase is arranged before and after Cr:1% on the contrary.At Ti content is the high reason of iron loss in the steel of tr., is considered to the result who causes hysteresis loss to increase owing to the carbide of separating out fine Cr.
2-2) the relation of .Ti/C and safe range of stress
The steel of smelting in testing laboratory contains Si:2.5%, Mn:0.18%, P:0.01%, S:0.002%, Al:0.7%, N:0.0010%, Cr:0.8%, changes the content of Ti and C, and Ti/C is changed, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 20%H 2-80%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, apply half organic membrane then, at 350 ℃ film is carried out sintering processes.For the driving condition of simulated machine, carry out the thermal treatment of 200 ℃ * 100hr, measure safe range of stress with following method then.
Just cut the sample of wide 5mm, long 150mm on the steel plate after the thermal treatment in parallel rolling direction, after the end parallel with rolling direction ground with No. 800 emery papers, with stress ratio be 0.1, the local pulse (stretching-stretching) of frequency 20Hz carries out fatigue test, in cycle index 10 7Condition under will not produce destructive stress amplitude as safe range of stress.
As shown in Figure 5, Ti/C is more than 1 as can be seen, and safe range of stress sharply increases, and almost reaches capacity when above 5.This phenomenon is considered to owing to add Ti C be combined with Ti, has suppressed the carbide of Cr and has separated out.Ti/C can cause magneticflux-density reduction, iron loss to increase above 30 words.
Therefore, guarantee Ti/C, reduce easily and Ti bonded S content is necessary as far as possible, require Mn/S 〉=10 more than 1.
3). contain the Mg steel
3-1) the relation of .Cr content and iron loss W10/600, magneticflux-density B50, Hv
The steel of smelting in testing laboratory contains C:0.0025%, Si:2.5%, Mn:0.20%, P:0.01%, S:0.002%, Al:1.3%, N:0.0021%, Mg:0.003%, Cr content is changed between tr.-6%, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 20%H 2-80%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, coated film is carried out sintering processes at 350 ℃ to film then.Measure the Hv of steel plate plate face, and measure W10/600, magneticflux-density B50 under the 600Hz with aforesaid method.
As shown in Figure 6, Cr:0.4-5% scope W10/600 significantly reduces as can be seen.This phenomenon is considered to because resistivity increases, and causes eddy losses reduction and magneticanisotropy to reduce to cause hysteresis loss to reduce both coefficient results.
Few for B50 is reduced, Cr is 0.4-1.4%, preferred 0.4-0.9%.
3-2) the relation of .Mg content and safe range of stress
The steel of smelting in testing laboratory contains C:0.0025%, Si:3.05%, Mn:0.20%, P:0.01%, S:0.002%, Al:1.05%, N:0.0018%, Cr:0.95%, Mg content is in the tr.-0.005% range, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min.Measure safe range of stress with aforesaid method then.
As shown in Figure 7, utilize as can be seen Mg content is added to more than 0.0001%, preferred more than 0.0005%, can improve safe range of stress.Mg content causes cost to increase above 0.005% words.With electron microscopic study add the effect of Mg, recognize owing to adding Mg to make thick Al 2O 3Piece reduces, so safe range of stress improves.
Under the situation of adding Mg, though be by above-mentioned control Ti/C safe range of stress to be improved, this also is because thick Al 2O 3The reason that piece reduces.
(embodiment 2)
With the processing that outgases of the molten steel of converter smelting, the steel 1-22 of composition shown in the melting table 2 is cast as slab, after heating under the 1140 ℃ * 1hr condition, carries out the hot-rolled steel sheet that thickness of slab 2.0mm is made in hot rolling.800 ℃ of final rolling temperatures, 610 ℃ of coiling temperatures during hot rolling.Hot-rolled steel sheet after batching is at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 20%H 2-80%N 2Atmosphere in carry out the final annealing of 900 ℃ * 1min, apply half organic membrane then, at 350 ℃ film is carried out sintering processes.For the driving condition of simulated machine, carry out the thermal treatment of 200 ℃ * 100hr, the magnetic properties when measuring Hv, 400Hz with aforesaid method then (W10/400, B50), safe range of stress.
The results are shown in table 2.
The W10/400 of steel 1-9 of the present invention is low, and the safe range of stress height.
On the other hand, do not contain the steel 10 of Cr and 14 W10/400 height.Ti/C is low less than the safe range of stress of 1 steel 10-12.Ti/C surpasses the W10/400 height of 30 steel 13.Si content surpasses 4% steel 15, Al content and surpasses 2% steel 16, Mn content to surpass the B50 of 2% steel 19 low.Mn content is less than the W10/400 height of 0.05% steel 17.Mn/S is less than the W10/400 height of 10 steel 18, and safe range of stress is low simultaneously.C content surpasses the W10/400 height of 0.005% steel 20, and safe range of stress is low simultaneously.N content surpasses the W10/400 height that 0.005% steel 21 and S content surpass 0.02% steel 22.
Table 2
Steel C Si Mn P S Al N Cr Ti Mn/S Ti/C W10/400 (W/kg) B50(T) Safe range of stress (MPa) Remarks
1 0.0020 2.50 0.18 0.018 0.0010 1.00 0.0011 0.90 0.003 180 1.5 17.70 1.65 330 Example
2 0.0020 2.50 0.18 0.018 0.0010 1.00 0.0012 0.90 0.008 180 4.0 17.50 1.65 340 Example
3 0.0020 2.50 0.17 0.010 0.0010 1.00 0.0010 0.90 0.010 170 5.0 17.60 1.65 345 Example
4 0.0030 2.50 0.18 0.011 0.0010 1.00 0.0010 0.90 0.020 180 6.7 17.80 1.65 346 Example
5 0.0016 2.50 0.18 0.010 0.0010 1.00 0.0011 0.50 0.008 180 5.0 17.60 1.65 335 Example
6 0.0020 2.50 0.17 0.015 0.0020 1.00 0.0010 0.90 0.008 85 4.0 17.50 1.65 341 Example
7 0.0020 2.50 0.17 0.010 0.0020 1.00 0.0010 1.40 0.008 85 4.0 17.80 1.65 343 Example
8 0.0020 2.50 0.18 0.010 0.0020 1.00 0.0013 2.00 0.008 90 4.0 17.90 1.64 352 Example
9 0.0020 2.50 0.18 0.018 0.0020 1.00 0.0010 4.00 0.008 90 4.0 18.00 1.63 355 Example
10 0.0020 2.50 0.18 0.018 0.0010 1.00 0.0015 tr. tr. 180 0.0 18.50 1.67 340 Comparative example
11 0.0020 2.50 0.18 0.018 0.0010 1.00 0.0020 0.90 tr. 180 0.0 18.60 1.66 300 Comparative example
12 0.0020 2.50 0.22 0.018 0.0010 1.00 0.0012 0.90 0.001 220 0.5 18.50 1.66 300 Comparative example
13 0.0015 2.50 0.18 0.011 0.0010 1.00 0.0015 0.90 0.050 180 33.3 19.00 1.63 350 Comparative example
14 0.0020 2.50 0.18 0.012 0.0010 1.00 0.0010 tr. 0.010 180 5.0 18.60 1.67 340 Comparative example
15 0.0025 4.20 0.18 0.018 0.0020 1.00 0.0022 0.90 0.010 90 4.0 16.40 1.61 396 Comparative example
16 0.0020 2.50 0.18 0.018 0.0020 2.50 0.0021 0.90 0.010 90 5.0 16.50 1.60 362 Comparative example
17 0.0022 2.50 0.02 0.020 0.0020 1.00 0.0010 0.90 0.010 10 4.5 18.70 1.64 356 Comparative example
18 0.0020 2.50 0.05 0.021 0.0070 1.00 0.0015 0.70 0.010 7 5.0 18.50 1.60 302 Comparative example
19 0.0020 2.50 2.25 0.021 0.0020 1.00 0.0019 0.70 0.010 1125 5.0 16.90 1.60 350 Comparative example
20 0.0060 2.00 0.18 0.025 0.0020 1.00 0.0020 0.70 0.020 90 3.3 21.00 1.64 250 Comparative example
21 0.0023 3.20 0.18 0.021 0.0020 1.00 0.0065 0.70 0.010 90 4.3 19.50 1.65 325 Comparative example
22 0.0022 2.50 0.18 0.020 0.0300 1.00 0.0021 0.70 0.010 6 4.5 19.30 1.63 355 Comparative example
(embodiment 3)
With the processing that outgases of the molten steel of converter smelting, the steel 1-22 of composition shown in the melting table 3 is cast as slab, after heating under the 1140 ℃ * 1hr condition, carries out the hot-rolled steel sheet that thickness of slab 2.0mm is made in hot rolling.800 ℃ of final rolling temperatures, 610 ℃ of coiling temperatures during hot rolling.Hot-rolled steel sheet after batching is at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 20%H 2-80%N 2Atmosphere in carry out the final annealing of 900 ℃ * 1min.Magnetic when measuring Hv, 600Hz with aforesaid method then (W10/600, magneticflux-density B50), safe range of stress.
The results are shown in table 3.
The W10/600 of steel 3-8 of the present invention, 11-15 is low, and the safe range of stress height.
On the other hand, the W15/50 height or the safe range of stress of comparative steel are low.
Table 3
Steel C Si Mn P S Al N Cr Mg W10/600 (W/kg) B50(T) Hv Safe range of stress (MPa) Remarks
1 0.0022 2.50 0.17 0.005 0.0010 1.50 0.0012 0.01 0.0003 40.00 1.67 190 350 Comparative example
2 0.0021 2.50 0.16 0.005 0.0010 1.50 0.0015 0.20 0.0003 39.50 1.67 190 350 Comparative example
3 0.0023 2.50 0.16 0.005 0.0010 1.50 0.0016 0.50 0.0003 33.80 1.67 192 352 Example
4 0.0029 2.50 0.17 0.005 0.0010 1.50 0.0024 0.95 0.0003 33.00 1.67 193 354 Example
5 0.0018 2.50 0.15 0.005 0.0010 1.50 0.0018 1.40 0.0003 32.00 1.66 195 355 Example
6 0.0026 2.50 0.15 0.005 0.0010 1.50 0.0015 1.80 0.0003 32.00 1.65 197 360 Example
7 0.0017 2.50 0.14 0.005 0.0010 1.50 0.0015 2.50 0.0003 32.50 1.64 200 362 Example
8 0.0016 2.50 0.18 0.005 0.0010 1.50 0.0015 4.50 0.0003 32.60 1.63 205 365 Example
9 0.0016 2.50 0.19 0.005 0.0010 1.50 0.0015 6.00 0.0003 35.20 1.62 210 370 Comparative example
10 0.0029 2.80 0.17 0.005 0.0020 1.20 0.0020 0.90 tr. 33.00 1.67 203 310 Comparative example
11 0.0028 2.80 0.17 0.005 0.0020 1.20 0.0021 0.90 0.0002 33.10 1.67 200 350 Example
12 0.0020 2.80 0.16 0.005 0.0020 1.20 0.0022 0.90 0.0003 33.05 1.66 200 360 Example
13 0.0022 2.80 0.17 0.005 0.0020 1.20 0.0024 0.90 0.0007 33.20 1.67 202 365 Example
14 0.0029 2.80 0.17 0.005 0.0020 1.20 0.0019 0.90 0.0020 33.10 1.66 203 365 Example
15 0.0020 2.80 0.17 0.005 0.0020 1.20 0.0024 0.90 0.0040 33.00 1.66 205 366 Example
16 0.0030 4.20 0.15 0.018 0.0020 1.00 0.0019 0.70 0.0007 34.00 1.61 230 400 Comparative example
17 0.0030 3.00 0.16 0.018 0.0020 2.50 0.0021 0.70 0.0007 32.00 1.60 190 360 Comparative example
18 0.0030 3.15 0.02 0.020 0.0020 0.80 0.0020 0.70 0.0007 40.50 1.64 210 370 Comparative example
19 0.0022 3.15 2.20 0.021 0.0020 0.80 0.0019 0.70 0.0007 31.50 1.62 230 400 Comparative example
20 0.0060 3.15 0.15 0.025 0.0020 0.80 0.0020 0.70 0.0006 40.05 1.64 210 370 Comparative example
21 0.0023 3.15 0.16 0.021 0.0020 0.80 0.0065 0.70 0.0007 41.05 1.63 210 370 Comparative example
22 0.0020 3.10 0.16 0.020 0.0300 0.80 0.0018 0.70 0.0007 41.20 1.63 200 360 Comparative example
The low non-oriented electromagnetic steel sheet of iron loss after the embodiment 3. high frequency stress relievings
The invention relates to special elementses such as utilize adding Cu, the non-oriented electromagnetic steel sheet that the iron loss behind the stress annealing is reduced.
1). the reason that composition limits
C: combine with Cr when being stress annealing, form the element of the carbide of Cr.The carbide of the Cr that forms is many, and the iron loss behind the stress annealing significantly raises, so require below 0.01%.
Si: can increase the resistivity of steel plate, thus be the effective element that reduces iron loss, little less than this effect under 1% situation.And reduce significantly above 4.0% words magneticflux-density.
Mn: the words magneticflux-density above 1% reduces significantly.
P: the words hardness above 0.05% obviously improves, and pressworkability worsens.In order to realize that effectively utilization as described later adds the effect that Cr reduces hardness, preferred P content is below 0.01%.
S: the words above 0.02% can be separated out MnS, and iron loss increases.
Al: identical with Si, be the element that steel plate resistivity is increased, but reduce significantly above 2% words magneticflux-density.Separate out fine AlN less than 0.1% words, hinder grain growth, iron loss is increased.
N: owing to separate out with the AlN form, and iron loss is increased, so require below 0.005%.
Cr: as the reason of narrating later, requiring Cr content is 0.2-5%.
As the reason of narrating later, also comprise at least a element among Cu:0.05-0.5%, Sb:0.002-0.1%, the Sn:0.002-0.1%.
All the other: be Fe basically.
2) relation of iron loss W10/400 behind .Cu content and the stress annealing
The steel of smelting in testing laboratory contains C:0.0025%, Si:2.5%, Mn:0.2%, P:0.01%, S:0.0015%, Al:1%, N:0.0012%, making Cr content is that tr. and 1%, Cu content change at tr.-0.6%, behind the above-mentioned steel hot rolling at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 950 ℃ * 1min, cut the ring-shaped sample of internal diameter 33mm, external diameter 45mm then, at 100%H 2Carry out the stress annealing of 750 ℃ * 2hr in the atmosphere, all around 100 circle leads, measure the W10/400 under the 400Hz then in primary winding one side and secondary coil one side.
As shown in Figure 8, Cr is under the situation of tr. as can be seen, even add Cu, W10/400 is also almost constant, and Cr content adds the Cu more than 0.05% under 1% situation, and W10/400 can reduce significantly.
Cu content is easy to generate surface imperfection above 0.5% words.Alleviating surface imperfection adding Ni is effectively, increases in order not cause iron loss, and preferred Ni add-on is below 0.5%.
3) relation of the W10/400 behind .Sb or Sn content and the stress annealing
Carry out test same as described above, and be used in Sb or Sn replaced C u that tr.-0.2% changes.
Shown in Fig. 9,10, the situation with Cu is identical as can be seen, and Cr is under the situation of tr., even add Sb or Sn, W10/400 is also almost constant, and on the other hand, Cr content adds Sb or the Sn of 0.002-0.1% under 1% situation, and W10/400 can reduce significantly.
4) relation of the W10/400 behind .Cr content and the stress annealing
The steel of smelting in testing laboratory contains C:0.0025%, Si:2.5%, Mn:0.2%, P:0.01%, S:0.0015%, Al:1%, N:0.0012%, making Cu content is that tr. and 0.2%, Cr content change at tr.-5%, tests with above-mentioned same method.
As shown in figure 11, Cu content think to add the tendency that Cr has some that W10/400 is increased, and Cu content is that 0.2-5% scope W10/400 significantly reduces at Cr that particularly Cr reduces significantly in the 0.4-1.4% scope under 0.2% situation under the tr. situation.
Cu, Sb, the two or more compound addings of Sn, also can behind stress annealing, obtain low W10/400 within the scope of the present invention.
The non-oriented electromagnetic steel sheet of above-mentioned embodiment 1-3 is only adjusted in the composition range of regulation, can use the method production identical with general non-oriented electromagnetic steel sheet.Just, adjust to the composition of regulation, casting back hot rolling under common condition with the processing that outgases of the molten steel of converter smelting.Directly carry out cold rolling then the steel plate after the hot rolling or annealing back cold rolling, perhaps insert process annealing carry out twice above cold rolling after, carry out final annealing again.Reducing when composition is adjusted under the inadequate situation of C content, during annealing after hot rolling or during final annealing, is 10-30 ℃ 5-30%H at dew point 2-all the other are N 2Atmosphere in carry out decarburization, also can reduce C content.
(embodiment 4)
With the processing that outgases of the molten steel of converter smelting, the steel 1-25 of composition shown in the melting table 4 is cast as slab, after heating under the 1140 ℃ * 1hr condition, carries out the hot-rolled steel sheet that thickness of slab 2.0mm is made in hot rolling.800 ℃ of final rolling temperatures, 610 ℃ of coiling temperatures during hot rolling.Hot-rolled steel sheet after batching is at 75%H 2-25%N 2Atmosphere in carry out the thermal treatment of 830 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 980 ℃ * 50sec.Cut the ring-shaped sample of internal diameter 33mm, external diameter 45mm then, at 100%H 2Carry out the stress annealing of 750 ℃ * 2hr in the atmosphere, all around 100 circle leads, measure W10/400, magneticflux-density B50 under the 400Hz then in primary winding one side and secondary coil one side.For the hot-rolled steel sheet after the batching of the steel in the table 47, at dew point+17 ℃ 10%H 2-90%N 2Atmosphere in, carry out the carbonization treatment of 720 ℃ * 1hr, carry out the thermal treatment of 860 ℃ * 3hr then.
It the results are shown in table 4.
Behind the steel 1-18 stress annealing of the present invention, obtain low W10/400.
On the other hand, Cu, Sb, Sn content steel 9,20 and the steel 21 of C content outside the scope of the invention outside the scope of the invention, the steel 22,23 of Cr content outside the scope of the invention, the steel 25 of Al content outside the scope of the invention, the W15/50 height behind the stress annealing.The magneticflux-density of the steel 24 of Mn content outside the scope of the invention is low in addition.
Table 4
Steel C Si Mn P S Al N Cr B Cu Ni Sb Sn W10/400 (W/kg) B50(T) Remarks
1 0.0018 2.5 0.18 0.010 0.0004 1.0 0.0012 1.0 tr. 0.07 0.01 tr. tr. 17.4 1.68 Example
2 0.0028 2.5 0.18 0.010 0.0012 1.1 0.0015 1.1 tr. 0.30 0.01 tr. tr. 16.7 1.67 Example
3 0.0014 2.4 0.19 0.010 0.0003 1.0 0.0010 0.9 tr. 0.30 0.30 tr. tr. 16.8 1.67 Example
4 0.0018 2.6 0.22 0.005 0.0015 1.0 0.0018 1.0 tr. 0.01 0.01 0.0024 tr. 17.6 1.68 Example
5 0.0016 2.5 0.18 0.007 0.0008 1.1 0.0024 1.1 tr. 0.01 0.01 0.012 tr. 17.0 1.68 Example
6 0.0030 2.4 0.16 0.012 0.0011 1.1 0.0014 1.0 tr. 0.01 0.01 0.05 tr. 16.5 1.68 Example
7 tr. 2.4 0.16 0.012 0.0011 1.0 0.0015 1.0 tr. 0.01 0.01 0.05 tr. 16.3 1.68 Example
8 0.0012 2.5 0.05 0.002 0.0005 1.0 0.0012 1.2 tr. 0.01 0.01 0.09 tr. 16.9 1.67 Example
9 0.0018 2.5 0.16 0.010 0.0002 1.0 0.0013 1.1 0.0008 0.01 0.01 0.05 tr. 16.8 1.67 Example
10 0.0017 2.5 0.21 0.015 0.0012 1.0 0.0016 1.0 tr. 0.10 0.10 0.02 tr. 16.7 1.67 Example
11 0.0022 2.5 0.12 0.012 0.0020 1.1 0.0014 1.0 tr. 0.01 0.01 tr. 0.03 17.2 1.68 Example
12 0.0014 1.3 0.35 0.020 0.0014 1.4 0.0012 1.4 tr. 0.01 0.01 0.05 tr. 17.8 1.69 Example
13 0.0013 3.4 0.02 0.004 0.0014 1.0 0.0012 0.9 tr. 0.01 0.01 0.04 tr. 15.2 1.62 Example
14 0.0015 2.5 0.14 0.015 0.0012 0.3 0.0015 1.1 tr. 0.01 0.01 0.05 tr. 17.8 1.69 Example
15 0.0013 2.5 0.18 0.012 0.0006 1.3 0.0014 0.25 tr. 0.01 0.01 0.04 tr. 17.3 1.70 Example
16 0.0019 2.4 0.15 0.010 0.0007 1.2 0.0012 0.43 tr. 0.01 0.01 0.05 tr. 17.0 1.69 Example
17 0.0012 2.5 0.12 0.008 0.0003 1.0 0.0015 1.5 tr. 0.01 0.01 0.05 tr. 17.2 1.66 Example
18 0.0024 2.5 0.12 0.007 0.0004 1.0 0.0011 4.5 tr. 0.01 0.01 0.05 tr. 17.8 1.62 Example
19 0.0023 2.5 0.17 0.012 0.0005 1.1 0.0015 1.0 tr. 0.01 0.01 tr. tr. 18.7 1.66 Comparative example
20 0.0022 1.3 0.35 0.020 0.0008 1.4 0.0017 1.4 tr. 0.01 0.01 tr. tr. 20.7 1.66 Comparative example
21 0.0120 2.5 0.18 0.014 0.0012 1.0 0.0021 1.1 tr. 0.01 0.01 0.05 tr. 19.5 1.68 Comparative example
22 0.0014 2.5 0.16 0.012 0.0014 1.0 0.0028 0.03 tr. 0.01 0.01 0.05 tr. 18.4 1.69 Comparative example
23 0.0012 2.5 0.16 0.009 0.0012 1.0 0.0021 5.8 tr. 0.01 0.01 0.05 tr. 18.0 1.61 Comparative example
24 0.0018 2.5 1.20 0.008 0.0009 1.1 0.0022 1.2 tr. 0.01 0.01 0.04 tr. 18.0 1.61 Comparative example
25 0.0019 2.5 0.20 0.008 0.0008 0.01 0.0022 1.3 tr. tr. 0.01 0.04 tr. 19.8 1.62 Comparative example
(embodiment 5)
The iron core of induction motor and direct-current machine turns blue 300-600 ℃ temperature range sometimes and handles and the hot charging processing with beyond the electrical sheet de-stress annealing.In order to observe the effect that adds Sb in such processing, smelted the steel 1-3 of composition shown in the table 5, used the method identical with embodiment 4, the steel plate behind finished products cuts ring-shaped sample, the sample of steel 2,3 is carried out the processing of 550 ℃ * 1hr again, measure W10/400 and B50.
The results are shown in table 5.
The steel 2 that does not add Sb turn blue handle after, W10/400 increases, even and the steel 3 that adds Sb also can obtain low W10/400 after handling turning blue, turn blue that to handle also be effective even add Sb as can be seen.This phenomenon is considered to owing to add Sb and suppressed to separate out at the carbide of the Cr when handling that turns blue.
The W10/400 of table 5 is than the W10/400 height of table 4, and this is that grain growth is insufficient because the temperature of the processing of turning blue is lower than stress relieving temperature.
Table 5
Steel C Si Mn P S Al N Cr B Cu Ni Sb Sn W10/400 (W/kg) B50(T) Remarks
1 0.0023 2.5 0.17 0.012 0.0005 1.0 0.0015 1.0 tr. tr. tr. tr. tr. 19.5 1.66 Behind the finished products
2 0.0023 2.5 0.17 0.012 0.0005 1.0 0.0015 1.0 tr. tr. tr. tr. tr. 20.5 1.66 Turn blue handle after
3 0.0025 2.5 0.17 0.012 0.0005 1.0 0.0016 1.0 tr. tr. tr. 0.05 tr. 19.2 1.66 Turn blue handle after
The non-oriented electromagnetic steel sheet of the low iron loss behind the embodiment 4. high frequency stress annealings
The invention relates to and utilize to reduce C content to obtain the non-oriented electromagnetic steel sheet of low iron loss behind the stress annealing.
1). the reason of determinant
C: the reason as the back is narrated requires below 0.0015%.
Si: the words magneticflux-density above 4.0% will reduce significantly.Owing to be that the resistivity of steel plate is increased, reduce the effective element of iron loss, so wish more than 1.0%.
Mn: the words magneticflux-density above 2% will reduce significantly.In order to prevent red brittleness, require more than 0.05%.
P: the words hardness above 0.1% significantly raises, and pressworkability worsens.
S: surpassing 0.02% words can the MnS form separate out, and iron loss increases.
Al: identical with Si, be the element that increases steel plate resistivity, the words magneticflux-density above 2% reduces significantly.Hope is more than 0.1%, to prevent causing iron loss to raise because of fine AlN separates out.
N: separate out with the AlN form, iron loss increases, and requires below 0.005%.
Cr: the reason as the back is narrated requires in the 0.4-5% scope.
All the other: be Fe basically.
2) relation of the iron loss W10/400 behind .C content and the stress annealing
The steel of smelting in testing laboratory contains C:0.0050%, Si:2.5%, Mn:0.18%, P:0.01%, S:0.0005%, Al:1.0%, N:0.0020%, Cr:1.0%, under the carbonization treatment condition shown in the table 6, decarburization is to the C content shown in the table 6 after the hot rolling.Then at 100%H 2Carry out the thermal treatment of 860 ℃ * 3hr in the atmosphere, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 1000 ℃ * 1min, cut the ring-shaped sample of internal diameter 33mm, external diameter 45mm then, at 100%H 2Carry out the stress annealing of 750 ℃ * 2hr in the atmosphere, all around 100 circle leads, measure the W10/400 under the 400Hz in primary winding one side and secondary coil one side.
As shown in figure 12, as seen make C content below 0.0015%, the W10/400 behind the stress annealing sharply reduces.C content can obtain lower W10/400 below 0.0009%.
C content is observed with scanning electronic microscope at the sample of 0.0003-0.0035%, observed the carbide of Cr on the sample of C content 0.0035% at crystal boundary and intracrystalline, do not observe the carbide of Cr at the sample of C content 0.0003%.Therefore C content is below 0.0015%, due to the carbide that the reason that W10/400 reduces has thought to suppress Cr is separated out.
Table 6
Processing No. Atmosphere Dew point (℃) Temperature (℃) C content (%) after the processing
A - - - 0.0050
B 15％H 2-85％N 2 25 750 0.0003
C 15％H 2-85％N 2 22 750 0.0005
D 15％H 2-85％N 2 20 750 0.0007
E 15％H 2-85％N 2 18 750 0.0009
F 20％H 2-80％N 2 18 750 0.0012
G 10％H 2-90％N 2 15 750 0.0014
H 15％H 2-85％N 2 15 750 0.0016
I 15％H 2-85％N 2 12 750 0.0018
J 15％H 2-85％N 2 10 750 0.0025
K 20％H 2-80％N 2 0 750 0.0035
L 15％H 2-85％N 2 -10 750 0.0042
3) relation of the W10/400 behind .Cr content and the stress annealing
The steel of smelting in testing laboratory contains C:0.0035%, Si:2.5%, Mn:0.18%, P:0.01%, S:0.0005%, Al:1.0%, N:0.0020%, Cr content is changed at tr.-5.5%, behind the above-mentioned steel hot rolling is 25 ℃ 15%H at dew point 2-85%N 2Atmosphere in carry out the decarburizing annealing of 750 ℃ * 2hr, making C content is 0.0005%.Then at 100%H 2Carry out the thermal treatment of 860 ℃ * 3hr in the atmosphere, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 1000 ℃ * 1min, measured the W10/400 behind the stress annealing with method same as described above then.
As shown in figure 13, Cr is more than 0.4% as can be seen, and particularly in the 0.4-1.4% scope, W10/400 significantly reduces.This phenomenon is considered to because the hysteresis loss that the eddy losses that the resistivity increase causes reduces to reduce to cause with magneticanisotropy reduces coefficient result.Increase and make lacking that B50 reduces in order to suppress cost, the Cr content requirement is below 5%.
The manufacture method of above-mentioned non-oriented electromagnetic steel sheet is as follows, to have Production Example such as quality % be C:0.005%, below the Si:4%, below the Al:2%, Mn:0.05-2%, below the P:0.1%, below the N:0.005%, below the S:0.02%, Cr:0.4-5%, all the other operations for the slab of Fe, and under the condition when producing non-oriented electromagnetic steel sheet usually, above-mentioned slab is carried out hot rolling, be cold rolled to after the pickling after the thickness of regulation, carry out the operation of continuous annealing, for the steel plate after the hot rolling or cold rolling after steel plate be 10-30 ℃ 5-30%H at dew point 2-all the other are N 2Atmosphere in carry out decarburization, C is dropped to below 0.0015%.
(embodiment 6)
With the processing that outgases of the molten steel of converter smelting, the steel 1-20 of composition shown in the melting table 7 is cast as slab, after heating under the 1140 ℃ * 1hr condition, carries out the hot-rolled steel sheet that thickness of slab 2.0mm is made in hot rolling.750 ℃ of final rolling temperatures, 610 ℃ of coiling temperatures during hot rolling.Hot-rolled steel sheet after batching is at 100%H 2Atmosphere in carry out the thermal treatment of 860 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 1000 ℃ * 1min.Then with W10/400, B50 behind the method mensuration stress annealing same as described above.
It the results are shown in table 7.
W10/400 behind the steel 1-9 stress annealing of the present invention is low, and the magneticflux-density height.
On the other hand, the steel 10 that Cr content is lower than the scope of the invention, steel 12-15, S and the steel 19,20 of N outside the scope of the invention that C content is higher than the scope of the invention, the W15/50 height behind the stress annealing.Cr, Si, Al, steel 11,16,17,18 magneticflux-densities that Mn content is higher than the scope of the invention are low in addition.
Table 7
Steel C Si Mn P S Al N Cr W10/400 (W/kg) B50(T) Remarks
1 0.0003 2.50 0.18 0.010 0.0003 0.98 0.0018 0.45 16.6 1.67 Example
2 0.0009 2.49 0.17 0.011 0.0004 1.02 0.0019 0.85 16.5 1.67 Example
3 0.0006 2.52 0.19 0.012 0.0005 1.00 0.0022 1.38 16.5 1.66 Example
4 0.0005 2.51 0.17 0.110 0.0005 1.01 0.0022 1.60 16.9 1.66 Example
5 0.0015 2.51 0.18 0.012 0.0006 1.01 0.0018 2.50 17.1 1.64 Example
6 0.0003 2.50 0.18 0.012 0.0003 0.99 0.0015 1.00 16.5 1.66 Example
7 0.0005 2.48 0.17 0.011 0.0007 1.00 0.0014 0.98 16.5 1.66 Example
8 0.0009 2.52 0.18 0.012 0.0005 0.98 0.0018 1.02 16.6 1.66 Example
9 0.0015 2.50 0.17 0.011 0.0003 1.03 0.0016 1.03 17.3 1.66 Example
10 0.0005 2.51 0.19 0.010 0.0003 1.02 0.0019 tr. 18.0 1.68 Comparative example
11 0.0007 2.49 0.17 0.011 0.0005 1.01 0.0022 5.50 17.3 1.58 Comparative example
12 0.0018 2.49 0.19 0.010 0.0004 0.99 0.0015 0.99 18.6 1.66 Comparative example
13 0.0025 2.50 0.18 0.012 0.0005 1.00 0.0013 1.01 18.9 1.66 Comparative example
14 0.0035 2.48 0.19 0.010 0.0007 1.01 0.0016 0.97 19.3 1.66 Comparative example
15 0.0050 2.50 0.18 0.011 0.0005 1.02 0.0018 1.00 20.0 1.66 Comparative example
16 0.0006 4.50 0.17 0.010 0.0004 0.30 0.0020 0.82 16.0 1.61 Comparative example
17 0.0007 2.47 0.19 0.011 0.0002 2.50 0.0018 1.03 16.6 1.60 Comparative example
18 0.0004 2.52 3.00 0.012 0.0003 0.99 0.0018 1.01 16.7 1.59 Comparative example
19 0.0005 2.51 0.17 0.011 0.0300 1.00 0.0022 1.00 19.5 1.65 Comparative example
20 0.0006 2.49 0.18 0.012 0.0005 1.02 0.0065 1.02 19.2 1.65 Comparative example
(embodiment 7)
Smelt the steel 1-3 shown in the table 8, use the method identical to cut ring-shaped sample, the sample of steel 2,3 is carried out processings of turning blue of 550 ℃ * 1hr again, mensuration W10/400 and B50 from the steel plate of finished products with embodiment 6.
The results are shown in table 8.
C content be 0.0030% steel 2 turn blue handle and finished products after W10/400 increase, also can obtain low W10/400 after handling even C content is 0.0005% steel 3 turning blue, though visible C content is significantly low, even also be effective through the processing of turning blue.This phenomenon is considered to because C content is low, and the carbide that has suppressed Cr when handling is separated out turning blue.
Table 8
Steel C Si Mn P S Al N Cr W10/400 (W/Kg) B50 (T) Remarks
1 0.0030 2.5 0.18 0.012 0.0003 1.0 0.0015 1.0 19.5 1.66 Behind the finished products
2 0.0030 2.5 0.18 0.012 0.0003 1.0 0.0015 1.0 20.5 1.66 Turn blue handle after
3 0.0005 2.5 0.18 0.012 0.0003 1.0 0.0016 1.0 19.0 1.66 Turn blue handle after
(embodiment 8)
With the processing that outgases of the molten steel of converter smelting, the steel 1-25 of composition shown in the melting table 9 is cast as slab, after heating under the 1140 ℃ * 1hr condition, carries out the hot-rolled steel sheet that thickness of slab 2.0mm is made in hot rolling.750 ℃ of final rolling temperatures, 610 ℃ of coiling temperatures during hot rolling.Hot-rolled steel sheet after batching is at 100%H 2Atmosphere in carry out the thermal treatment of 860 ℃ * 3hr, be cold rolled to thickness of slab 0.35mm, at 10%H 2-90%N 2Atmosphere in carry out the final annealing of 1000 ℃ * 1min.Before thermal treatment or during the final annealing of cold rolling back, carry out decarburizing annealing with the condition shown in the table 10, with reduction C content to the hot-rolled steel sheet of a part of steel after batching this moment.Then with W10/400, B50 behind the method mensuration stress annealing same as described above.
The results are shown in table 10.
W10/400 behind the steel 1-12 stress annealing of the present invention is low, and the magneticflux-density height.
On the other hand, the steel 13 that Cr content is lower than the scope of the invention, C content steel 15-20, S and N the W15/50 height steel 24, the 25 stress annealings scope of the invention beyond after higher than the scope of the invention.Cr, Si, Al, steel 14,21,22,23 magneticflux-densities that Mn content is higher than the scope of the invention are low in addition.
Table 9
Steel C Si Mn P S Al N Cr
1 0.0039 2.51 0.19 0.012 0.0003 1.00 0.0015 0.45
2 0.0048 2.50 0.18 0.011 0.0005 0.99 0.0019 0.86
3 0.0040 2.51 0.19 0.012 0.0004 1.01 0.0018 1.35
4 0.0047 2.48 0.18 0.011 0.0005 0.98 0.0016 1.60
5 0.0039 2.51 0.19 0.011 0.0005 1.00 0.0018 2.48
6 0.0047 2.49 0.19 0.012 0.0003 1.01 0.0016 0.90
7 0.0038 2.50 0.18 0.011 0.0002 1.00 0.0015 0.95
8 0.0045 2.49 0.19 0.012 0.0004 1.01 0.0018 0.97
9 0.0047 2.51 0.17 0.011 0.0003 1.00 0.0022 1.00
10 0.0048 2.49 0.19 0.012 0.0004 1.01 0.0018 0.98
11 0.0045 2.52 0.17 0.110 0.0005 0.99 0.0020 0.99
12 0.0042 2.50 0.18 0.011 0.0005 1.00 0.0016 1.01
13 0.0040 2.49 0.17 0.011 0.0005 1.02 0.0018 tr.
14 0.0045 2.00 0.17 0.011 0.0005 1.01 0.0015 5.46
15 0.0020 2.52 0.17 0.011 0.0005 0.99 0.0016 0.98
16 0.0045 2.50 0.18 0.012 0.0004 1.00 0.0021 1.05
17 0.0045 2.51 0.19 0.012 0.0003 1.01 0.0018 0.99
18 0.0035 2.51 0.18 0.011 0.0005 1.00 0.0022 1.40
19 0.0035 2.51 0.19 0.011 0.0005 1.00 0.0020 1.40
20 0.0035 2.51 0.18 0.011 0.0005 1.00 0.0022 1.40
21 0.0042 4.50 0.17 0.010 0.0004 0.30 0.0013 0.82
22 0.0032 2.47 0.19 0.011 0.0002 2.50 0.0016 1.03
23 0.0040 2.52 2.95 0.012 0.0002 0.99 0.0018 1.01
24 0.0045 2.51 0.17 0.011 0.0300 1.00 0.0020 1.00
25 0.0039 2.48 0.18 0.012 0.0010 1.02 0.0065 1.03
Table 10
Steel Carbonization treatment C amount (%) after the decarburization W10/400 (W/kg) B50(T) Remarks
During processing Atmosphere Dew point (℃) Temperature (℃) Time
1 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0003 16.6 1.67 Example
2 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0005 16.5 1.67 Example
3 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0006 16.5 1.66 Example
4 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0010 16.9 1.66 Example
5 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0005 17.1 1.65 Example
6 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0003 16.5 1.66 Example
7 Hot-roll annealing 15％H 2-85％N 2 22 750 2hr 0.0005 16.5 1.66 Example
8 Hot-roll annealing 15％H 2-85％N 2 18 750 2hr 0.0009 16.5 1.66 Example
9 Hot-roll annealing 10％H 2-90％N 2 18 750 2hr 0.0015 16.6 1.66 Example
10 Finished products 20％H 2-80％N 2 25 700 1min 0.0014 16.6 1.66 Example
11 Finished products 15％H 2-85％N 2 20 750 5min 0.0008 16.5 1.66 Example
12 Finished products 10％H 2-90％N 2 15 800 10min 0.0003 16.5 1.66 Example
13 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0005 18.0 1.68 Comparative example
14 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0009 17.3 1.58 Comparative example
15 - - - - - 0.0021 18.6 1.66 Comparative example
16 - - - - - 0.0046 19.2 1.66 Comparative example
17 Hot-roll annealing 15％H 2-85％N 2 12 750 2hr 0.0018 18.6 1.66 Comparative example
18 Hot-roll annealing 15％H 2-85％N 2 10 750 2hr 0.0025 18.9 1.66 Comparative example
19 Hot-roll annealing 20％H 2-80％N 2 0 750 2hr 0.0035 19.3 1.66 Comparative example
20 Hot-roll annealing 15％H 2-85％N 2 -10 750 2hr 0.0048 20.0 1.66 Comparative example
21 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0006 16.0 1.61 Comparative example
22 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0007 16.6 1.60 Comparative example
23 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0004 16.7 1.59 Comparative example
24 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0005 19.5 1.65 Comparative example
25 Hot-roll annealing 15％H 2-85％N 2 25 750 2hr 0.0005 19.2 1.65 Comparative example

Claims (5)

1. non-oriented electromagnetic steel sheet, containing quality % is C:0.0016-0.0029%, Si:2.5-3.0%, Mn:0.14-0.20%, P:0.005-0.01%, S:0.001-0.002%, Al:1.0-1.5%, N:0.0012-0.0024%, Cr:0.4-5%, Mg:0.0001-0.005%, and all the other are Fe.
2. non-oriented electromagnetic steel sheet as claimed in claim 1, Cr content are 0.4-1.4%.
3. the manufacture method of a non-oriented electromagnetic steel sheet, comprise operation: quality % is that C:0.005% is following containing, Si:2.48-2.52%, Al:0.98-1.02%, Mn:0.17-0.19%, P:0.010-0.110%, N:0.0014-0.0022%, S:0.0003-0.0007%, Cr:0.4-5%, and all the other make slab for the steel of Fe; Pickling after the above-mentioned slab hot rolling, be cold rolled to specific thickness then, carry out continuous annealing again; To the steel plate after the hot rolling or cold rolling after steel plate carry out carbonization treatment, make C content at 0.0003-0.0015%.
4. the manufacture method of non-oriented electromagnetic steel sheet as claimed in claim 3, wherein the carbonization treatment of carrying out makes C content at 0.0003-0.0009%.
5. as the manufacture method of each described non-oriented electromagnetic steel sheet in claim 3 or 4, wherein use slab with Cr:0.4-1.4% replaced C r:0.4-5%.
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JP4280224B2 (en) * 2004-11-04 2009-06-17 新日本製鐵株式会社 Non-oriented electrical steel sheet with excellent iron loss
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CN105886932B (en) * 2016-05-09 2017-08-25 武汉钢铁有限公司 A kind of High Power Factor Non-oriented silicon steel for motors and production method
CA3051823C (en) 2017-02-07 2022-07-12 Jfe Steel Corporation Method for producing non-oriented electrical steel sheet, method for producing motor core, and motor core
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