CN1026597C - Iron-based soft magnetic material - Google Patents
Iron-based soft magnetic material Download PDFInfo
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- CN1026597C CN1026597C CN89109231A CN89109231A CN1026597C CN 1026597 C CN1026597 C CN 1026597C CN 89109231 A CN89109231 A CN 89109231A CN 89109231 A CN89109231 A CN 89109231A CN 1026597 C CN1026597 C CN 1026597C
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- Prior art keywords
- iron
- flux density
- soft magnetic
- present
- steel
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Dispersion Chemistry (AREA)
- Power Engineering (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Soft Magnetic Materials (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
This invention relates to an iron base, soft magnetic steel material which has high direct current magnetization, can be produced magnetic core and magnetism screen material. The steel material of this invention contains 0.5 to 2.5 % of Al, not more than 1.0 % of Si, not more than 0.007% of C+N,not more than 0.5% of Mn and not more than 0.005% of oxygen, the rest being Fe and unavoidable impurities. Its ferrite crystal grain size is at least 0.5 mm, its magnetic flux density is at least 11,000 G at 0.5 Oe under the state where a lattice strain is removed sufficiently, its magnetic flux density is at least 15,500 G at 25 Oe and its coercive force is up to 0.4 Oe.Thus,it has excellent high direct current magnetization and can be magnetized easily in weak magnetic field.So it is suitable to be used as high performance iron core and magnetism screen material.
Description
The present invention relates to the iron-based soft magnetic material that electro-magnet core material, magnetic shielding material etc. require high dc magnetizing characteristic.
As DC electromagnet core material or progressive in recent years and universal express medicine equipment and magnetic shielding materials such as various physical instrument, electronic unit and equipment, what adopt at present is cheap soft iron and pure iron and high permalloy (hypermalloy) or the supermalloy (ferronickel molybdenum manganese super-permalloy) of price that obtains.And soft iron and pure iron are at 79.6A/m(1 Oe) time magneticflux-density (to call the B value in the following text) be approximately 0.3-1.1T(3000-11000G) about, the tomography that they are used as the MRI(nucleus magnetic resonance resembles the photography diagnostic device) number Gausses such as magnetic shielding about magnetic shielding material, or electromagnet core material.
In utilizing the important use of dc magnetizing characteristic, be the problem that example explanation prior art exists with the magnetic shielding.Promptly, though in the MRI magnetic shielding, use the cheap and high pure iron of saturation magnetization of price at present, but for being the electromagnetism soft iron of object with soft iron, pure iron, characteristic requires the tightest O kind (being specially JIS C 2504 SUYPO) even regulation B in the JIS of Japanese Industrial Standards standard
1The lower limit of value is at 0.8T(8000G) below, the magnetic shielding that will reach the earth magnetism degree under the situation of this specific character is difficult, but also the shielding harness for the following magnetic shielding of several approximately Gausses is increased the weight of and thickization.As the shielding material that can better shield, sometimes also use permalloy or supermalloy, though these materials can carry out the following shielding of earth magnetism degree, yet but there is price very high, and saturation magnetization is than the low 1/3-2/3 of pure iron, therefore, must increase shortcomings such as thickness greatly when the shielding upfield, it is uneconomic using these materials in a word in a large number.
Based on above-mentioned situation, quite a lot of tests have been done for neither damaging the research that high saturation and magnetic intensity that pure iron class material had can improve permeability again.For example, special public clear 63-45443 number, the spy opens clear 62-77420 number, or disclosed method all is to improve as target with the permeability that the ferrite coarsening is followed in Japanese Metallkunde meeting the 23rd volume No. 5 (distribution in 1984) " exploitation of extremely thick electro-magnetic steel plate ", yet these technology all are that to be limited to object be the thin hot-rolled sheet technology of thickness of slab, or can not be as in the present invention, further estimating strict dc magnetizing characteristic at 39.8A/m(0.5Oe) time magneticflux-density (to call B in the following text
0.5Value) can reach 1.1T(11000G) above technology, because they are not the technology that can obtain good dc magnetizing characteristic, so they all are incomplete.
The saturation magnetization height can not be provided before above information slip makes eye bright and in the quite low magnetic field of earth magnetism degree, demonstrate high magnetic flux density, be i.e. the high material of permeability.Purpose of the present invention just is to provide this material.
In order to solve problem, present inventors have at first studied as the armos iron of direct magnetic field with the soft magnetic material basis, get clear further to study after its shortcoming again and seek to improve its characteristic, and the result obtains following view.
That is to say, found: consider from obtaining the high permeability viewpoint, by adding Al, 1. deoxidation effectively, along with the minimizing of oxygen amount and oxide-based inclusion not only can improve permeability, and since the AlN particulate form and can also reduce the solid solution N that permeability is had disadvantageous effect; 2. pass through the interpolation of certain necessary amount, can make fine dispersive AlN particle aggregationization, when doing one's utmost to force down AlN particle disadvantageous effect, by working the annealing operation of eliminating the lattice distortion effect, can also obtain significantly to promote the effect of ferrite crystal grain alligatoring, they all are effective to improving permeability; 3. particularly, the solvable Al of acid adds above 0.85%, transformation temperature is significantly improved, perhaps can make it to become the single-phase body of ferrite, therefore can not import the distortion that phase transformation causes, and might anneal, and this annealing can be removed lattice distortion effectively and make ferrite crystal grain thick above under 900 ℃ of temperature, though can think that solid solution Al itself also has the effect that improves permeability, also should relate to is because the effect that multiplies each other of these effects obtains the extremely magnetic diffusivity of excellence; 4. also can add an amount of Ti as required, these Ti can make solid solution N preferentially fixing, thereby help to improve characteristic, and the content that particularly at all needn't make great efforts to reduce N can achieve the goal; And from keeping high saturation magnetization viewpoint to consider; 5. should avoid the addition of Al to surpass 2.5%; 6. since C, N content for a long time transformation temperature can reduce and maybe need strengthen necessary Al addition, the lattice distortion meeting strengthens or generates carbide, nitride along with the increase of solid solution C, N, therefore tend to make characteristic to degenerate, the upper limit should be arranged for avoiding these situations C, N amount; The present invention promptly is based on above discovery and finishes.
First invention that is to say the application provides a kind of iron-based soft magnetic material, it is characterized in that representing with weight %, it is by the solvable Al:0.85-2.5% of acid, below the Si:1.0%, below the C+N:0.007%, below the Mn:0.5%, oxygen: below 0.005%, surplus is that Fe and unavoidable impurities are formed, and the ferrite crystal grain particle diameter is more than 0.5mm, 39.8A/m(0.5Oe under the state of fully eliminating lattice distortion) flux density value the time is 1.1T(11000G) more than, the flux density value in the time of 1990A/m(25Oe) is at 1.55T(15500G) more than, coercive force is 31.8A/m(0.4Oe) below.
Second invention of the present invention provides a kind of iron-based soft magnetic material, it is characterized in that by below the solvable Al:0.85-2.5%Si:1.0% of acid, below the C+N:0.014%, below the Mn:0.5%, oxygen: below 0.005%, Ti:0.005-1.0%, surplus is that Fe and inevitable impurity are formed, and the ferrite crystal grain particle diameter is more than the 0.5mm, 39.8A/m(0.5Oe under the state of fully eliminating lattice distortion) flux density value the time is 1.1T(11000G) more than, at 1990A/m(25Oe) time flux density value be 1.55T(15500G) more than, coercive force is 31.8A/m(0.4Oe) below.
Below the reason of limit forming among the present invention is illustrated
The content of C and N wishes that in order to ensure good dc magnetizing characteristic the content of C and N is low as far as possible, is very difficult but reduce to their content extremely low in the industrial production, and its result can cause cost high on the contrary.And, both made owing to can improve transformation temperature by adding Al, if but the addition of C, N is not controlled at very lowly, then the essential addition of Al might increase, and consequently makes the saturation magnetization reduction, and is opposite with wish of the present invention.Fig. 2 is that the variation of dc magnetizing characteristic is with B after eliminating lattice distortion by the annealing under 1000-1100 ℃ the common normal condition
0.5When the variation of value was represented, research C+N amount was to the graphic representation of magneticflux-density influence.As seen from the figure, in order to obtain good characteristic, the C+N amount must be below 0.007%.Therefore, stipulate below the C+N:0.007% among the present invention.
Among the present invention, as described below, also can add Ti as required, it is the powerful element that generates nitride.Ti at all needn't carry out strict upper bound control to the N amount that interrelates with expensive, and is the element that purpose is added with the disadvantage of eliminating above-mentioned N, therefore in this case, is limited to 0.014% on the C+N amount.
Though Si helps to improve permeability, but also pass through the later thick ferrite crystal grain that can obtain more than the 0.5mm of suitable annealing by adding Al among the present invention, therefore not as considering that heavy addition Si can cause saturation magnetization to reduce, cost raises, and its upper limit is defined as 1.0%.
Mn is the element that dc magnetizing characteristic is worsened, so wishes to reduce its content, can cause cost to raise and the increase of N content but extremely reduce Mn.In addition, S is fixing also to prevent hot short effect owing to make, and therefore in Mn/S was not less than 10 scope, the upper limit of its content also can be 0.50%.
Al, as mentioned above, it is main adding elements of the present invention, it can cause the rising of fixing and AlN particle aggregationization and the transformation temperature of solid solution N, because the ferrite zone is enlarged, therefore can reach thickization of ferrite crystal grain and reduce lattice distortion by annealing, consider that in addition solid solution Al itself also has the effect that improves dc magnetizing characteristic, so Al be that the present invention is the element of the essential interpolation of the good dc magnetizing characteristic of acquisition institute.As shown in Figure 1, under the state of the solvable Al of acid addition in the effect that can demonstrate this Al more than 0.5%, yet sour solvable Al is lower than at 0.85% o'clock, C+N but can not obtain enough dc magnetizing characteristics when measuring within the scope of the present invention high value.But then, if addition can make saturation magnetization reduce above 2.5% and cause B
25Value reduces, and this is undesirable, so the addition scope of Al is defined as 0.85-2.5% under the solvable Al state of acid.
As mentioned above, Ti is the powerful element that generates nitride, because the scope of addition is 0.005-1.0%, has therefore both made in N content is not fully reduced promptly the material in cheapness, because the fixed effect of solid solution N and can avoid significantly damaging dc magnetizing characteristic.And the growing amount of nitride particles is also few when N content is low, therefore can expect that also dc magnetizing characteristic has some raisings.On the other hand, if addition surpasses above-mentioned higher limit, can cause that then dc magnetizing characteristic worsens.
The chemical ingredients that limits according to the present invention can obtain B as mentioned above
0.5Value and B
25Be worth high, i.e. good steel of soft magnetic property in the direct magnetic field.
As the steel of object of the present invention, comprise the hot-work steel as mentioned above, cold or warm working steel products; And the kind of steel comprises slab, thin plate, web (shape steel etc.), forges material etc.
The present invention's steel can be used the hot worked method of strand as mentioned above, strand is directly carried out temperature processing or cold worked method, carry out cold working or warm method for processing after the hot-work, vertical compression hot rolled method, and the whole bag of tricks manufacturings such as method of anneal in these method courses of processing (common more than 450 ℃), but all these methods all will be carried out final annealing.This final annealing preferably carries out under 1000-1300 ℃ of temperature generally more than 900 ℃.
Embodiment
Table 1 illustrates the chemical ingredients of used steel in the present invention and the comparative example.
Grade of steel is C-G, J, and L, N-T, V-X, Z are the steel grades that meets the present invention's composition, and grade of steel is A, and H, I, K, M, U, Y, a are the contrast steel grades.Table 2 is that the steel ingot that thickness is 110mm is made in the melting of steel grade shown in the table 1 later on, and it is carried out the hot rolling of 1200 ℃ of heating, is rolled into the steel plate that thickness is 15mm, after the annealing, measures its dc magnetizing characteristic and ferrite crystal grain grain warp, and the result converges into table 2.Annealing is the hold-time to be 1-3 hour in heating, carries out under about 100 ℃/hour-500 ℃/hour usual terms of speed of cooling.
In the table 2, No.1-8 and No.20 example are the influences of the sour solvable Al amount of investigation.No.20 is the Comparative Examples of pure iron.Fig. 1 is the curve that compiles these results.
No.9-12 and No.24 example are the influences of investigation C+N amount.Fig. 2 adds the result of No.3 example again and puts in order out on these results.Can find out thus, under the situation of not adding Ti, B then when C+N amount surpasses 0.007%
0.5Value worsens.
The No.13-15 example is the influence of investigation Mn amount, can think that dc magnetizing characteristic has the tendency of deterioration along with the increase of Mu amount, if but the Mn amount is no more than 0.5% scope, infer that generally good characteristic still can guarantee.
The No.16-19 example is the influence of investigation Si.It is generally acknowledged that the increase saturation magnetization along with the Si amount also decreases, so that magneticflux-density (B
0.5Value, B
1Value, B
25Value) reduces, but still can guarantee good characteristic.In addition, well-known, the interpolation of Si, identical with Al, the intrinsic impedance of steel is increased, therefore be applied to be processed into thin plate through cold rolling grade, when being used for soft magnetic material that AC magnetic field uses, can expect has the effect that reduces iron loss.
No.21-23, No.25, the No.26 example is the influence that Ti is added in investigation.It is generally acknowledged that thereby can fix N by interpolation Ti obtains good characteristic.No.22 example particularly, be to be equivalent to the No.10(Comparative Examples) example of the present invention of having added Ti in the steel, and the No.25 example is to be equivalent to the No.24(Comparative Examples) steel in added Ti example of the present invention, although C+N in these examples＞0.007%, but the abundant fix N of energy owing to added Ti, with No.10, the No.24 Comparative Examples is compared as can be seen, and its characteristic has significantly to be improved.
Table 3 is certain several steel in the his-and-hers watches 1, after cold rolling becomes thin plate, through behind the common annealing, investigates the result of its dc magnetizing characteristic in the same manner with the embodiment of table 2 in hot rolling.The cold roling reduction of the cold rolling material shown in these examples of the present invention and the Comparative Examples is 50-80%.
In the table 3, No.1 and No.2 are to be the Comparative Examples of U steel with steel grade.And No.3-5 is the present invention's embodiment.These the present invention's examples are compared with the Comparative Examples of No.1 and No.2, demonstrate good dc magnetizing characteristic.
Again, no matter be in the table 2 or in the table 3, have the example of the present invention of good dc magnetizing characteristic, its all ferritic size of microcrystal are all more than 0.5mm.
As mentioned above, the present invention's soft magnetic material has good dc magnetizing characteristic, even thereby in extremely weak magnetic field, also can be easy to make it magnetization, be the extremely useful material that makes high function core material or high function magnetic shielding material.
Description of drawings:
Fig. 2 is expression C+N content and dc magnetizing characteristic (B
0.5Value) graphic representation of relation, Fig. 1 are sour solvable Al addition of expression and dc magnetizing characteristic (B
0.5Value, B
25Value) graphic representation of relation.
Claims (2)
1, a kind of iron-based soft magnetic material, it is characterized in that it by, (% meter by weight), the solvable Al:0.85-2.5% of acid, below the Si:1.0%, below the C+N:0.007%, below the Mn:0.5%, oxygen: below 0.005%, surplus is that Fe and unavoidable impurities are formed, and, the ferrite crystal grain particle diameter is more than the 0.5mm, and under the state that lattice distortion is fully eliminated, the flux density value that demonstrates when 39.8A/m (0.5Oe) is more than the 1.1T (11000G), flux density value when 1990A/m (25Oe) is more than the 1.55T (15500G), and coercive force is below 31.8A/m (0.4 Oe).
2, a kind of iron-based soft magnetic material, it is characterized in that it is by (% by weight), the solvable Al:0.85-2.5% of acid, below the Si:1.0%, below the C+N:0.014%, below the Mn:0.5%, oxygen: below 0.005%, Ti:0.005-1.0%, surplus is that Fe and unavoidable impurities are formed, and, the ferrite crystal grain particle diameter is more than the 0.5mm, demonstrate at 39.8A/m(0.5Oe under the state that lattice distortion is fully eliminated) time flux density value be 1.1T(11000G) more than, the flux density value in the time of 1990A/m(25Oe) is 1.55T(15500G) more than, coercive force is at 31.8A/m(0.4Oe) below.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP155026/89 | 1989-06-17 | ||
| JP1155026A JP2679258B2 (en) | 1989-06-17 | 1989-06-17 | Iron-based soft magnetic steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1048237A CN1048237A (en) | 1991-01-02 |
| CN1026597C true CN1026597C (en) | 1994-11-16 |
Family
ID=15597047
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN89109231A Expired - Fee Related CN1026597C (en) | 1989-06-17 | 1989-12-08 | Iron-based soft magnetic material |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0429651B1 (en) |
| JP (1) | JP2679258B2 (en) |
| KR (1) | KR970004566B1 (en) |
| CN (1) | CN1026597C (en) |
| CA (1) | CA2020464A1 (en) |
| DE (1) | DE68913544T2 (en) |
| WO (1) | WO1990016076A1 (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04265580A (en) * | 1991-02-20 | 1992-09-21 | Fujitsu Ltd | Magnetic disk device |
| JP2503125B2 (en) * | 1991-05-09 | 1996-06-05 | 新日本製鐵株式会社 | Manufacturing method of good electromagnetic plate |
| JP2503124B2 (en) * | 1991-05-09 | 1996-06-05 | 新日本製鐵株式会社 | Manufacturing method of good electromagnetic thick plate |
| DE4293604T1 (en) * | 1991-10-14 | 1994-07-21 | Nippon Kokan Kk | Soft magnetic steel material with excellent direct field magnetization properties as well as excellent corrosion resistance and process for its production |
| JPH0770715A (en) * | 1993-09-01 | 1995-03-14 | Nkk Corp | Soft magnetic steel excellent in strain resistance and production thereof |
| JPH0790505A (en) * | 1993-09-27 | 1995-04-04 | Nkk Corp | Soft magnetic steel material and its production |
| CN100334246C (en) * | 2004-05-28 | 2007-08-29 | 宝山钢铁股份有限公司 | False-proof coinage steel and producing method thereof |
| CN103789609A (en) * | 2014-02-13 | 2014-05-14 | 山西太钢不锈钢股份有限公司 | Method for manufacturing electromagnetic pure iron |
| CN104294150B (en) * | 2014-10-30 | 2016-05-18 | 武汉钢铁(集团)公司 | Steel and production method thereof for shielding line |
| KR101977507B1 (en) * | 2017-12-22 | 2019-05-10 | 주식회사 포스코 | Steel sheet for magnetic field shielding and method for manufacturing the same |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60208418A (en) * | 1984-03-30 | 1985-10-21 | Sumitomo Metal Ind Ltd | Production of thick steel plate having high magnetic permeability for structural member |
| JPS60207418A (en) * | 1984-03-30 | 1985-10-19 | 株式会社東芝 | Device for protecting main circuit |
| JPS60208417A (en) * | 1984-03-30 | 1985-10-21 | Sumitomo Metal Ind Ltd | Production of hot-rolled high magnetic permeability iron sheet |
-
1989
- 1989-06-17 JP JP1155026A patent/JP2679258B2/en not_active Expired - Fee Related
- 1989-12-08 WO PCT/JP1989/001232 patent/WO1990016076A1/en active IP Right Grant
- 1989-12-08 EP EP90900342A patent/EP0429651B1/en not_active Expired - Lifetime
- 1989-12-08 CN CN89109231A patent/CN1026597C/en not_active Expired - Fee Related
- 1989-12-08 DE DE68913544T patent/DE68913544T2/en not_active Expired - Fee Related
- 1989-12-08 KR KR1019910700178A patent/KR970004566B1/en not_active IP Right Cessation
-
1990
- 1990-06-18 CA CA002020464A patent/CA2020464A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| EP0429651B1 (en) | 1994-03-02 |
| JP2679258B2 (en) | 1997-11-19 |
| JPH0320447A (en) | 1991-01-29 |
| WO1990016076A1 (en) | 1990-12-27 |
| EP0429651A1 (en) | 1991-06-05 |
| EP0429651A4 (en) | 1991-12-04 |
| KR970004566B1 (en) | 1997-03-29 |
| KR920700458A (en) | 1992-02-19 |
| DE68913544T2 (en) | 1994-07-21 |
| DE68913544D1 (en) | 1994-04-07 |
| CA2020464A1 (en) | 1990-12-18 |
| CN1048237A (en) | 1991-01-02 |
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