CN105714192B - Soft magnetism steel, soft magnetism steel part and its manufacture method having excellent electromagnetic properties - Google Patents
Soft magnetism steel, soft magnetism steel part and its manufacture method having excellent electromagnetic properties Download PDFInfo
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- CN105714192B CN105714192B CN201510925592.2A CN201510925592A CN105714192B CN 105714192 B CN105714192 B CN 105714192B CN 201510925592 A CN201510925592 A CN 201510925592A CN 105714192 B CN105714192 B CN 105714192B
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Mechanical Engineering (AREA)
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- Electromagnetism (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Soft Magnetic Materials (AREA)
Abstract
The present invention relates to a kind of soft magnetism steel having excellent electromagnetic properties, soft magnetism steel part and its manufacture method, it passes through Mn content control is in low degree and adds B and suppresses exaggerated grain growth, the soft magnetism steel having excellent electromagnetic properties of one aspect of the present invention, in terms of weight %, comprising：C：0.001~0.02%, Mn：0.05~0.10%, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：0.001~0.004%, N：0.002~0.005%, surplus Fe and other inevitable impurity, also, micro organization is single-phase ferrite, it includes MnS and BN miscible precipitate, and the miscible precipitate is the shape that BN coats MnS.
Description
Technical field
The present invention relates to a kind of soft magnetism steel having excellent electromagnetic properties of the electric equipment parts available for automobile etc., soft
Magnet steel part and its manufacture method.
Background technology
In order to improve the energy efficiency based on environmental legislation, it is necessary to improve the electric equipment parts steel of automobile etc.
Electromagnetic property.For example, this electric equipment parts have the pole segment (pole of generator, magnetic valve, alternator rotor
) or pawl pole (claw pole) etc. segment.Electromagnetic property needed for electric equipment parts steel has high magnetic permeability, Gao Ci
Flux density and low iron loss etc..Also, according to the purposes and shape of the part utilized, it is necessary to a certain degree more than intensity and
Hot forging and forging.Thus it is common to use the magnetic flux density of steel easily response external magnetic field and meets intensity and forging
The low-carbon steel of property.
In the past, compared to the improvement of the material property of low-carbon steel, more focus on being based on part itself outward appearance and design effect
Electric equipment parts high efficiency.Recently, headed by automotive field, to part outward appearance and electric equipment parts
The requirement more and more higher of improvement material property for the purpose of high performance.
In order to improve the performance of the electric equipment parts steel, alternatively it is conceivable to utilize the soft magnetism steel of pure iron system
The method of (JIS-SUYB1 etc.).The soft magnetism steel of pure iron system have the ultra-low carbon steel material that carbon content is below 0.02 weight %
Single phase ferrite, so as to have excellent electromagnetic properties, but exists after hot forging or cold forging because of abnormal grain for heat treated article
Grow (abnormal grain growth) and cause the problem of electromagnetic property is deteriorated.
In order to prevent exaggerated grain growth, in the patent document 1 of the related invention of electrical sheet, in order to prevent it is cold rolling it
Exaggerated grain growth when being annealed afterwards, utilizes MnS, AlN, MnSe etc..
But, it is different from electrical sheet, for semi-finished product such as wire rod and bars, it will subsequently carry out hot forging or cold forging-annealing
Process.Thus, the inhomogeneous deformation produced by forging can promote exaggerated grain growth, and because this micro organization will aggravate
The reduction of electromagnetic property.
Even if it is then desired to develop a kind of process for carrying out hot forging or cold forging-annealing, can also prevent exaggerated grain growth
The soft magnetism steel having excellent electromagnetic properties, soft magnetism steel part and its manufacture method.
Prior art literature
(patent document 1) Korean Patent Laid the 2002-0043690th
The content of the invention
(1) technical problem to be solved
According to requirement as described above, it is an object of the invention to provide a kind of soft magnetism steel having excellent electromagnetic properties and soft
Magnet steel part and its manufacture method, it passes through Mn content control is in low degree and adds B and suppresses exaggerated grain growth.
(2) technical scheme
The soft magnetism steel having excellent electromagnetic properties of one aspect of the present invention, in terms of weight %, comprising：C：0.001~
0.02%th, Mn：0.05~0.10%, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：0.001~
0.004%th, N：0.002~0.005%, surplus Fe and other inevitable impurity, also, micro organization is single-phase iron element
Body, it includes MnS and BN miscible precipitate, and the miscible precipitate is the shape that BN coats MnS.
Also, the manufacture method of the soft magnetism steel having excellent electromagnetic properties of another aspect of the present invention includes：1000
The step of being heated at a temperature of~1200 DEG C to the steel billet for meeting foregoing composition；By to heated described
Steel billet carries out the step of hot rolling is to obtain steel；And with 0.1~10 DEG C/sec of cooling velocity to by the steel of hot rolling
The step of being cooled down.
Also, the soft magnetism steel part having excellent electromagnetic properties of an additional aspect of the present invention, it meets above-mentioned composition, micro-
Single-phase ferrite is carefully organized as, and includes MnS and BN precipitate, the miscible precipitate is the shape that BN coats MnS, and it is put down
Equal size is below 35nm, magnetic flux density B10For more than 1.2Tesla.
Also, the manufacture method of the soft magnetism steel part having excellent electromagnetic properties of an additional aspect of the present invention includes：770
The step of steel of the invention are heated at a temperature of~1200 DEG C；By carrying out hot forging to the heated steel
The step of to obtain hot forging；The step of being cooled down with 0.1~10 DEG C/sec of cooling velocity to the hot forging；And it is right
The step of cooled hot forging carries out cold forging.
It should be noted that the technical scheme of above-mentioned solution described problem does not enumerate the technical characteristic of the present invention all.
It is more detailed that the various technical characteristics of the present invention and the advantage and effect based on technical characteristic can refer to following embodiment
Carefully understand.
(3) beneficial effect
The present invention has the effect of the electromagnetic property for the soft magnetism steel for improving the electric equipment parts for being used as automobile etc..It is logical
Crossing improves this electromagnetic property and can realize miniaturization and the high precision int of electric equipment parts, and passes through what these were produced
Weight minimizing effect and with improving the effect of the environmental protection such as fuel efficiency.
Brief description of the drawings
Fig. 1 is the mean size for the miscible precipitate for representing MnS based on Mn contents and BN in the steel added with B
Figure.
Fig. 2 is transmission electron microscope (TEM) photo of the precipitate of example 3 and the composition ideograph of precipitate.
Fig. 3 is the chart for the precipitate property varied with temperature for representing example 3.
Preferred embodiment
Ultra-low carbon steel material of the soft magnetism steel by carbon content for below 0.02 weight % has single phase ferrite, and
Because the amount of the carbide for the growth (pinning effect) for playing a part of preventing crystal boundary is few, therefore after being recrystallized at high temperature
The fast growth of crystal grain.
Also, if soft magnetism wire rod and bar make annealing treatment after hot forging or cold forging, then due to magnetically soft steel
The amount of precipitate inside material is few, can produce because of uneven microstructure phenomenon caused by exaggerated grain growth.Because of abnormal grain life
The micro organization that long and thick crystal grain and fine-grain is mixed can cause the dislocation density of intra-die to have differences.This
The reason for high deviation of the difference and grain size of planting dislocation density turns into the uneven magnetic flux flows in steel, so as to cause
The electromagnetic property deterioration of final products.
The present inventor confirms that this uneven microstructure can reduce the electromagnetic property of final part, in order to solve the above problems,
MnS precipitates are refined by adjusting Mn addition, and BN precipitates are utilized by adding B, so as to confirm by suppression
The exaggerated grain growths of soft magnetism steel processed improves electromagnetic property, and has been finally completed the present invention.
Hereinafter, the soft magnetism steel having excellent electromagnetic properties of one aspect of the present invention are described in detail.
The soft magnetism steel having excellent electromagnetic properties of one aspect of the present invention, in terms of weight %, comprising：C：0.001~
0.02%th, Mn：0.05~0.10%, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：0.001~
0.004%th, N：0.002~0.005%, surplus Fe and other inevitable impurity, also, micro organization is single-phase iron element
Body, includes MnS and BN miscible precipitate, and the miscible precipitate is the shape that BN coats MnS, its mean size be 35nm with
Under.
Hereinafter, to the constituent of limitation steel the reasons why, illustrates.(following, the unit of the content of each element is
Weight %.)
Carbon (C)：0.001~0.02 weight %
C is solid-solution in steel or formed carbide etc..Preferably, for the excellent magnetic characteristic of soft magnetism steel, by carbon
Content is controlled in extremely low amount.When C content is more than 0.02 weight %, magnetic characteristic is reduced because forming carbide, when containing for C
When measuring as less than 0.001 weight %, the production efficiency of steel is reduced.Thus, C content is preferably 0.001~0.02 weight %.
Manganese (Mn)：0.05~0.1 weight %
Mn is important composition in the present invention, plays a part of suppressing exaggerated grain growth by forming MnS.But
It is, when Mn contents add excessive more than 0.1 weight %, easily to form thick MnS.Because MnS has the crystalline substance that BN is separated out
The effect of kind of (seed), therefore thick MnS forms thick MnS and BN miscible precipitate, so as to cause electromagnetic property bad
Change.Thus, the upper limit of Mn contents is preferably 0.1 weight %, more preferably 0.95 weight %, much further preferably from 0.9
Weight %.
Also, when addition is less than 0.05 weight %, it is difficult to the content of manganese is controlled, when addition is few, due to not
Form MnS, it is thus possible to can turn into and the reason for high temperature deformation is cracked is produced caused by S.Thus, the lower limit of Mn contents is preferably
0.0 weight 5%.
Silicon (Si)：0.1~0.7 weight %
Si is effective element for reducing the iron loss caused by vortex flow, therefore in order to improve electromagnetic property and extensive use.
Also, Si also acts as the effect of deoxidier, with the effect for suppressing to cause magnetic characteristic to reduce because of the oxygen in steel, therefore Si
Addition is preferably more than 0.1 weight %.But, when Si additions are more than 0.7 weight %, there is saturation flux density reduction
Shortcoming.Thus, Si content is preferably 0.1~0.7 weight %.
Phosphorus (P)：Below 0.02 weight %
The phosphorus is the impurity inevitably contained, it is preferable that by the control of its content as low as possible.Although in theory
In 0 weight % it is than advantageous, but inevitably to contain in manufacturing process by the control of the content of phosphorus.It is important that
Upper control limit, is preferably limited to 0.02 weight % by the upper limit of the phosphorus content in the present invention.Also, when the content of the P
During less than 0.001 weight %, the manufacturing expense of refinery practice can be significantly increased, therefore, it is highly preferred that by the content control of the P
System is in 0.001%~0.02 weight %.
Sulphur (S)：0.002~0.1 weight %
S is the element inevitably contained in manufacturing process, it is therefore important that controlling the upper limit.For this hair
For bright Mn addition is 0.05~0.1 weight % steel, the upper limit for controlling S is even more important.When S addition surpasses
When crossing 0.01 weight %, the S will not all consume a remaining part for MnS, thus can produce the high temperature deformation caused by S
Cracking.Also, in order to play a part of the present invention to be realized suppress exaggerated grain growth by MnS, preferably add
More than 0.002 weight %.Thus, S content is preferably 0.002~0.01 weight %.
Boron (B)：0.001~0.004 weight %
B fixes N by forming BN, so as to prevent the embrittlement of the electromagnetic property caused by N.Also, play by being formed
BN suppresses the effect of exaggerated grain growth.In order to form preferred addition more than the 0.001 weight % of BN and fixed N effect, when
There is the tendency of effect saturation when addition is more than 0.004 weight %, therefore B content is preferably 0.001~0.004 weight
Measure %.
Nitrogen (N)：0.002~0.005 weight %
Due to the brittle electromagnetic property of N meetings, therefore it is preferably addition as a small amount of as possible, but in manufacturing process unavoidably
Contain on ground.It is important that controlling the upper limit, the upper limit of the nitrogen content is preferably limited to 0.005 weight in the present invention
Measure %.Also, when the content of the N is less than 0.002 weight %, the manufacturing expense of increase refining procedure can be significantly increased, and
And suppress that the effect of exaggerated grain growth is also insufficient by forming BN, therefore be more preferably to control the content of the N
In 0.002~0.005 weight %.
Remaining composition of the present invention is iron (Fe).But, can not from raw material or surrounding environment in general manufacturing process
It is mixed into impurity with avoiding, therefore can not excludes.On these impurity, as long as the technical staff in general manufacturing process can
Enough know, therefore be not specifically mentioned all the elements about this respect in this manual.
And, it is preferable that the micro organization of the steel is single-phase ferrite.Because pearlite or carbide etc. can be hindered
Electromagnetic property, exists with the state of solid solution it is preferred that being added to the carbon of steel and forms single-phase ferrite.
Also, the steel include MnS and BN miscible precipitate, the miscible precipitate is the shape that BN coats MnS.
The reasons why being separated out with shape as described above be because MnS Precipitation Temperature is high and MnS is first separated out, separate out MnS it
After separate out BN.
Also, the mean size of MnS and BN miscible precipitate is preferably below 35nm.
When the mean size of the miscible precipitate is more than 35nm, electromagnetic property can be deteriorated.Because when described multiple
It is hot forging or cold in part manufacturing process when the mean size for closing precipitate forms thick miscible precipitate more than 35nm
Exaggerated grain growth can not be suppressed in forging-annealing process, so as to cause electromagnetic property to deteriorate.Thus, MnS and BN compound precipitation
The mean size of thing is preferably below 35nm.
To make precipitate prevent exaggerated grain growth, precipitate should be with sufficiently amount and suitably big in operating condition
It is small to be uniformly distributed.And should not become thick without reducing electromagnetic property by precipitate in the final product.
Also, the phase content of the MnS and BN miscible precipitates is preferably 0.01~0.05 area %.
When the phase content of the miscible precipitate is less than 0.01 area %, can not effectively it press down because the amount of precipitate is not enough
Exaggerated grain growth processed.Also, when phase content is more than 0.05 area %, it is possible to play the nonmetallic folder of reduction electromagnetic property
The effect of debris, thus it is not preferred.Thus, the phase content of MnS and BN miscible precipitates is preferably 0.01~0.05 area %.
Also, the steel are preferably wire rod or bar shape.
It is different from electrical sheet, it is follow-up to carry out hot forging or cold forging-annealing operation for semi-finished product such as wire rod and bars.By
This, the inhomogeneous deformation produced by forging can promote exaggerated grain growth, and because this micro organization can aggravate electromagnetism spy
The reduction of property.Thus, when steel are wire rod or bar shape, the effect of suppression exaggerated grain growth of the invention can be brighter
It is aobvious.
Hereinafter, the manufacture method to the soft magnetism steel having excellent electromagnetic properties of another aspect of the present invention is carried out in detail
Explanation.
The manufacture method of the soft magnetism steel having excellent electromagnetic properties of another aspect of the present invention, including：1000~
The step of being heated at a temperature of 1200 DEG C to the steel billet for meeting above-mentioned composition；By entering to the heated steel billet
The step of row hot rolling is to obtain steel；And with 0.1~10 DEG C/sec of cooling velocity to described cold by the steel progress of hot rolling
But the step of.
Heating stepses
The steel billet for meeting the component system is heated at a temperature of 1000~1200 DEG C.Due in the temperature
In the range of steel billet is heated, so as to effectively dissolving remaining segregation, carbide and field trash.When the steel billet
The efficiency of production operation is low when heating-up temperature is more than 1200 DEG C.On the other hand, heating is passed through when heating-up temperature is less than 1000 DEG C
The effect reached may be insufficient.Here, steel billet refers to the semi-finished product that can be made into wire rod or bar, such as bloom
Or small billet (billet) etc. (bloom).
The step of by hot rolling to obtain steel
Can be to implementing hot rolling by the heated steel billet of mode as described above.When rolling temperature is less than 800 DEG C, because
Fine ferrite crystal grain may reduce electromagnetic property.On the other hand, when rolling temperature is more than 1100 DEG C, because of austenite crystal
Become mechanical-physical character that is thick and hindering wire rod and bar.It is thus preferred that carrying out heat at a temperature of 800~1100 DEG C
Roll.
Cooling step
Preferably, the wire rod that hot rolling is carried out by mode as described above is cooled down.Now, when cooling velocity is less than
At 0.1 DEG C/sec, the exaggerated grain growth in cooling procedure can be encouraged, and cause surface characteristic because forming oxide skin (scale)
Reduction.On the other hand, when cooling velocity is more than 10 DEG C/sec, the growth of crystal grain is suppressed, so that electromagnetic property can be reduced.Thus,
Preferably, the cooling velocity should meet 0.1~10 DEG C/sec of scope.For the cooled wire rod of easily keeping and movement,
The step of being wound is may also include after the cooling step.
Hereinafter, the soft magnetism steel part having excellent electromagnetic properties of an additional aspect of the present invention is described in detail.
The soft magnetism steel part of another aspect of the present invention meets above-mentioned composition, and micro organization is single-phase ferrite, bag
MnS and BN miscible precipitate are included, also, the miscible precipitate is the shape that BN coats MnS.
Meet the magnetic flux density B of alloy composition as described above and the soft magnetism steel part of micro organization10For 1.2Tesla with
On, show excellent electromagnetic property.
Also, the mean size of MnS and BN miscible precipitate is preferably below 35nm in soft magnetism steel part.When described
When the mean size of miscible precipitate is more than 35nm, electromagnetic property can be deteriorated.
Hereinafter, the manufacture method to the soft magnetism steel part of an additional aspect of the present invention is described in detail.
The manufacture method of the soft magnetism steel part having excellent electromagnetic properties of an additional aspect of the present invention includes：770~
The step of steel of the invention are heated at a temperature of 1200 DEG C；By the heated steel are carried out hot forging come
The step of obtaining hot forging；The step of being cooled down with 0.1~10 DEG C/sec of cooling velocity to the hot forging；And to institute
State the step of cooled hot forging carries out cold forging.
Now, it is preferable that the heating and hot forging are carried out at a temperature of 770~1200 DEG C.When with adding less than 770 DEG C
When hot temperature is heated, because of flow stress height, hot forging effect is low, and when heating-up temperature is more than 1200 DEG C, MnS and BN are by again
Solid solution, it is thus low come the effect for suppressing exaggerated grain growth by separating out MnS and BN during the forging of the invention to be reached.
Now, it is preferable that the cooling is carried out with 0.1~10 DEG C/sec of speed.When cooling velocity is less than 0.1 DEG C/sec
When, the exaggerated grain growth in cooling procedure can be encouraged, and surface characteristic is reduced because forming oxide skin.When cooling velocity exceedes
At 10 DEG C/sec, suppress the growth of crystal grain, so as to reduce electromagnetic property.
Afterwards, the magnetically soft steel portion having excellent electromagnetic properties can be manufactured by carrying out cold forging to the cooled hot forging
Part.
In addition, further being carried out after the cold forging step at a temperature of 560~790 DEG C to described by cold forging
The step of steel are heat-treated, thus can manufacture the soft magnetism steel part having excellent electromagnetic properties.
Now, it is preferable that the heat treatment after the cold forging is carried out at a temperature of 560~790 DEG C.Because working as
When heat treatment temperature is less than 560 DEG C, the speed for eliminating internal stress is slow, and the improvement of electromagnetic property is low after heat treatment, when
During more than 790 DEG C, recrystallization is produced by phase transformation, electromagnetic property thus can be reduced.
Embodiment
Below, the more specific explanation present invention of embodiment is passed through.But, the following examples are to be intended merely to further in detail
Describe the bright present invention in detail and example, be not used to limit protection scope of the present invention.Protection scope of the present invention is according to power
Content described in sharp claim and the content thus rationally derived are determined.
The steel for the component system being documented in following tables 1 is cast.Then the temperature according to general method at 1150 DEG C
Degree is lower to be heated and carries out hot rolling and produce a diameter of 50mm bar respectively.Then at a temperature of 1050 DEG C with 5 DEG C/
The speed of second by a diameter of 50mm of hot rolling bar to being cooled down.
The pole piece (pole segment) (or pawl pole) of motor vehicle alternator rotor is manufactured using the bar.Will be straight
Footpath is cut with 1.2kg weight and heated at a temperature of 1200 DEG C for 50mm bar, and by four steps
To this progress hot forging.Epithelium processing is carried out after hot forging, then cold forging is implemented by three steps.
Mean size to the MnS and BN of the bar miscible precipitate, forged by method as described above plus
Whether the electromagnetic property of the processed goods of work and the generation of mixed grain structure are observed, and the results are shown in table 1.
It is that 45mm, internal diameter are the annular that 35mm, thickness are 10mm by taking out external diameter in forge piece for electromagnetic property
Magnet coil (solenoid) test piece is observed, and copper cash is wound into the circle of primary coil (primary) 100, secondary coil
(secondary) magnetic flux density during H=1000A/m is defined as by B-H (magnetic flux density-magnetic field intensity) curve after 20 circles
B10And be shown in Table 1 below.
Also, for whether producing mixed grain structure, in following table 1, during with the observation by light microscope of x50 multiplying powers,
If crystal grain quantity more than ASTM class 4s is differed compared with mean grain size accounts for more than the 20% of total crystal grain quantity, evaluate
To generate mixed crystal and being represented with O, if less than 20%, then represented with X.
Also, Fig. 1 represents being averaged in the steel added with the B MnS and BN of the changes of contents with Mn miscible precipitate
Size, Fig. 2 represents to enter the precipitate in the steel using the extraction of extraction replica (Replica) method by transmission electron microscope
The result of row observation, Fig. 3 represents the precipitate property varied with temperature of the steel grade of the composition with example 3.
[table 1]
The unit of the content of each element is weight % in the table 1.
Pass through the table 1, the magnetic flux density B of example 1 to example 310For 1.22~1.24, with comparative example 1 to 7
Magnetic flux density B10Being compared for 0.97~1.11 has excellent electromagnetic property.This is due to that example 1 to example 3 meets this
The alloy composition of invention, i.e., Mn content is low and with the addition of B.Thus, ensured excellent by effectively suppressing exaggerated grain growth
Electromagnetic property.
The mean size of MnS and BN miscible precipitate is represented in Fig. 1 and the table 1 with the result of Mn changes of contents
In.Below 0.05~0.1 weight % example 1 to 3, the mean size of MnS and BN miscible precipitates are met for Mn contents
For 22.5~31.3nm, it is known that this nano-precipitation prevents from exaggerated grain growth to improve electromagnetic property.
Also, be solid-solution in the N in steel by adding B and be fixed to BN, thus improve electromagnetic property while, MnS and
BN miscible precipitate suppresses exaggerated grain growth, thus improves electromagnetic property.
In comparative example 1, Mn contents are not up to the scope of the Mn contents of the present invention, MnS are not sufficiently formed, so as to generate
Because of the mixed crystal phenomenon of exaggerated grain growth, and the embrittlement of the electromagnetic property caused by S is produced, cause electromagnetic property to deteriorate.
In comparative example 2, S contents be not up to the present invention S contents scope, be not sufficiently formed MnS, thus generate because
The mixed crystal phenomenon of exaggerated grain growth, so as to cause electromagnetic property to deteriorate.
Comparative example 3 to comparative example 5 is the situation that Mn contents exceed the scope of Mn contents of the invention and added too much,
The mean size of MnS and BN miscible precipitates is thick for more than 58.5nm, therefore can not suppress the generation of mixed crystal, and reduction magnetic
Flux density.
When meeting the Mn contents proposed in example of the present invention and addition B, as shown in Figure 2, it is known that BN claddings are positioned at center
MnS.Fig. 2 is the result using the precipitate in the steel of replication extraction by transmission electron microscope observation.In Fig. 2
Middle comparison of light and shade it is deep for precipitate, the dark colour at precipitate center is MnS, and the light colour of precipitate periphery is BN.
Understand precipitate with Fig. 2 by Fig. 3 precipitate property calculated with thermodynamics popular software Thermocalc
Form the reasons why separate out.Property to the precipitate variation with temperature of the steel grade of the composition with example 3 is observed,
As a result understand because MnS Precipitation Temperature Gao Erxian is precipitated, BN is separated out after MnS is separated out.Entered by transmission electron microscope
, also there is MnS or BN single precipitate in the result of row observation, but the fraction of MnS and BN miscible precipitates is high.Understand, when
During without fine adjusting MnS, it can not play a part of suppressing exaggerated grain growth because of thick precipitate, causing electromagnetism special
Property reduction.
Comparative example 6 and comparative example 7 are the situations for the steel grade for not adding B, it is known that it is not formed not only for suppressing different
The BN of normal grain growth, and cause magnetic flux density to deteriorate because of solid solution N.Understand by that can not be kept away in the production process by steel
The impurity N being mixed into exempting from is separated out with BN can improve electromagnetic property.
Above by reference to embodiment, the present invention is described, but those skilled in the art is it will be appreciated that without departing from power
Various modifications and changes can be carried out in the range of the thought of the invention of sharp claim record and field.
Claims (12)
1. a kind of soft magnetism steel having excellent electromagnetic properties, in terms of weight %, comprising：C：0.001~0.02%, Mn：0.05~
0.10%th, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：0.001~0.004%, N：0.002~
0.005%th, surplus Fe and other inevitable impurity, also, micro organization is single-phase ferrite, and include MnS and BN
Miscible precipitate, the miscible precipitate be BN coat MnS shape.
2. the soft magnetism steel according to claim 1 having excellent electromagnetic properties, it is characterised in that the MnS's and BN is compound
The phase content of precipitate is 0.01~0.05 area %.
3. the soft magnetism steel according to claim 1 having excellent electromagnetic properties, it is characterised in that the miscible precipitate it is flat
Equal size is below 35nm.
4. the soft magnetism steel according to claim 1 having excellent electromagnetic properties, it is characterised in that the steel are wire rod or rod
Material shape.
5. a kind of manufacture method for the soft magnetism steel having excellent electromagnetic properties, it includes：
The step of being heated at a temperature of 1000~1200 DEG C to steel billet, the steel billet, in terms of weight %, comprising：C：
0.001~0.02%, Mn：0.05~0.10%, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：
0.001~0.004%, N：0.002~0.005%, surplus Fe and other inevitable impurity；
By carrying out the step of hot rolling is to obtain steel to the heated steel billet；And
The step of with 0.1~10 DEG C/sec of cooling velocity to being cooled down by the steel of hot rolling.
6. the manufacture method of the soft magnetism steel according to claim 5 having excellent electromagnetic properties, it is characterised in that the steel
It is wire rod or bar shape.
7. a kind of soft magnetism steel part having excellent electromagnetic properties, in terms of weight %, comprising：C：0.001~0.02%, Mn：0.05~
0.10%th, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：0.001~0.004%, N：0.002~
0.005%th, surplus Fe and other inevitable impurity, also, micro organization is single-phase ferrite, and include MnS and BN
Miscible precipitate, the miscible precipitate be BN coat MnS shape, magnetic flux density B10For more than 1.2Tesla.
8. the soft magnetism steel part according to claim 7 having excellent electromagnetic properties, it is characterised in that fine group of the part
It is woven to the crystal grain quantity differed compared with mean grain size more than ASTM class 4s and is less than 20%.
9. the soft magnetism steel part according to claim 7 having excellent electromagnetic properties, it is characterised in that the MnS's and BN answers
The phase content for closing precipitate is 0.01~0.05 area %.
10. the soft magnetism steel part according to claim 7 having excellent electromagnetic properties, it is characterised in that the MnS's and BN answers
The mean size for closing precipitate is below 35nm.
11. a kind of manufacture method for the soft magnetism steel part having excellent electromagnetic properties, including：
The step of being heated at a temperature of 770~1200 DEG C to steel, wherein, the steel, in terms of weight %, comprising：
C：0.001~0.02%, Mn：0.05~0.10%, Si：0.1~0.7%, P：Less than 0.02%, S：0.002~0.01%, B：
0.001~0.004%, N：0.002~0.005%, surplus Fe and other inevitable impurity, also, micro organization is
Single-phase ferrite, it includes MnS and BN miscible precipitate, and the miscible precipitate is the shape that BN coats MnS；
By carrying out the step of hot forging is to obtain hot forging to the heated steel；
Cooling step is carried out to the hot forging with 0.1~10 DEG C/sec of cooling velocity；And
The step of cold forging is carried out to the cooled hot forging.
12. the manufacture method of soft magnetism steel part according to claim 11,560 are additionally included in after the cold forging step
The step of at a temperature of~790 DEG C to being heat-treated by the steel of cold forging.
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| KR10-2014-0187372 | 2014-12-23 | ||
| KR1020140187372A KR101657815B1 (en) | 2014-12-23 | 2014-12-23 | Soft magnetic steel and soft magnetic part having excellent electromagnetic properties, and method for manufacturing the same |
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| CN112680656B (en) * | 2020-11-27 | 2023-04-14 | 中天钢铁集团有限公司 | Boron-containing steel for motor claw pole and low-cost smelting process thereof |
| WO2023084756A1 (en) * | 2021-11-12 | 2023-05-19 | Ｊｆｅスチール株式会社 | Soft magnetic iron |
| JP7239075B1 (en) * | 2021-11-12 | 2023-03-14 | Ｊｆｅスチール株式会社 | Electromagnetic soft steel bar |
| WO2023171362A1 (en) * | 2022-03-10 | 2023-09-14 | 株式会社神戸製鋼所 | Soft-magnetic wire, soft-magnetic steel bar, and soft-magnetic component |
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| KR100501004B1 (en) | 2000-12-02 | 2005-07-18 | 주식회사 포스코 | A method for manufacturing high magnetic flux density grain-oriented electrical steel sheet |
| JP4223726B2 (en) | 2002-02-06 | 2009-02-12 | 株式会社神戸製鋼所 | Soft magnetic steel material excellent in cold forgeability and magnetic permeability characteristics, soft magnetic steel part excellent in magnetic permeability characteristics and manufacturing method thereof |
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