CN116162868A - Medium nickel soft magnetic alloy and preparation method thereof - Google Patents
Medium nickel soft magnetic alloy and preparation method thereof Download PDFInfo
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- CN116162868A CN116162868A CN202310060923.5A CN202310060923A CN116162868A CN 116162868 A CN116162868 A CN 116162868A CN 202310060923 A CN202310060923 A CN 202310060923A CN 116162868 A CN116162868 A CN 116162868A
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- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 93
- 229910001004 magnetic alloy Inorganic materials 0.000 title claims abstract description 45
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 44
- 238000002360 preparation method Methods 0.000 title abstract description 12
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 111
- 239000000956 alloy Substances 0.000 claims abstract description 111
- 230000035699 permeability Effects 0.000 claims abstract description 37
- 238000000034 method Methods 0.000 claims abstract description 27
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 12
- 239000000126 substance Substances 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims description 65
- 238000004321 preservation Methods 0.000 claims description 49
- 238000000137 annealing Methods 0.000 claims description 27
- 238000005096 rolling process Methods 0.000 claims description 27
- 238000001816 cooling Methods 0.000 claims description 25
- 238000005242 forging Methods 0.000 claims description 25
- 238000011534 incubation Methods 0.000 claims description 9
- 230000006698 induction Effects 0.000 abstract description 26
- 238000012545 processing Methods 0.000 abstract description 19
- 238000004519 manufacturing process Methods 0.000 abstract description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 16
- 239000002609 medium Substances 0.000 description 16
- 239000011651 chromium Substances 0.000 description 14
- 239000011572 manganese Substances 0.000 description 14
- 239000010955 niobium Substances 0.000 description 14
- 230000008092 positive effect Effects 0.000 description 14
- 239000012535 impurity Substances 0.000 description 10
- 238000003723 Smelting Methods 0.000 description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 8
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 8
- 229910052804 chromium Inorganic materials 0.000 description 8
- 229910052742 iron Inorganic materials 0.000 description 8
- 229910052748 manganese Inorganic materials 0.000 description 8
- 229910052758 niobium Inorganic materials 0.000 description 8
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 8
- 229910052710 silicon Inorganic materials 0.000 description 8
- 239000010703 silicon Substances 0.000 description 8
- 230000005415 magnetization Effects 0.000 description 7
- 230000002159 abnormal effect Effects 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 230000009471 action Effects 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 230000005389 magnetism Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
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- 238000006243 chemical reaction Methods 0.000 description 1
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- -1 foreign 45H Inorganic materials 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000010365 information processing Effects 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000013630 prepared media Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
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- 230000008054 signal transmission Effects 0.000 description 1
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
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- 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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- 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
- C21D8/1272—Final recrystallisation annealing
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Abstract
The application relates to the technical field of alloy preparation, in particular to a medium nickel soft magnetic alloy and a preparation method thereof. The chemical components of the alloy comprise: ni, cr, nb, mn, si, C, fe; wherein, the content of Ni is 47.50 to 49.00 weight percent, the content of Cr is 0.10 to 0.50 weight percent, the content of Nb is 0.01 to 0.20 weight percent, the content of Mn is 0.10 to 0.50 weight percent, the content of Si is 0.05 to 0.30 weight percent, and the content of C is less than 0.01 weight percent. The content of the application solves the technical problems that the existing medium nickel soft magnetic alloy is difficult to simultaneously consider high magnetic induction performance and low remanence performance, and the alloy has certain constant magnetic permeability, and compared with the traditional constant magnetic induction alloy processing and preparing method, the preparation method has the advantages of short processing flow, small limitation on production equipment and processing modes and the like.
Description
Technical Field
The application relates to the technical field of alloy preparation, in particular to a medium nickel soft magnetic alloy and a preparation method thereof.
Background
Soft magnetic alloys are a class of alloys that have high magnetic permeability and low coercivity in weak magnetic fields. The alloy is widely applied to the radio and electronic industry, precise instruments and meters, remote control and automatic control systems, and is mainly used for two aspects of energy conversion and information processing.
The existing medium nickel soft magnetic alloy (Ni content is 40% -60%, mass percent) is such as national standard 1J46 and 1J50 alloy, national army standard 1J48 alloy, foreign 45H, PB alloy and the like, and the saturated magnetic induction Bs is generally not more than 1.55T, so that the miniaturized design requirement of electromagnetic devices cannot be met. And has a low magnetic permeability (mu) m Not more than 100 mH/m), which easily results in reduced sensitivity of the electromagnetic device to signal effects when the material is applied to the electromagnetic device. In addition, the magnetic induction of the magnetically soft alloy is improved, and meanwhile, the residual magnetism of the magnetically soft alloy is correspondingly improved, for example, in the previously developed high-magnetic induction medium nickel magnetically soft alloy BYR48, although the Bs of the magnetically soft alloy is up to 1.58T, the magnetically soft alloy has certain high magnetic induction characteristic, the residual magnetism is higher (Br=1.0T), the hysteresis of an electromagnetic device is easy to cause, and the magnetic permeability difference of the BYR48 alloy under different magnetic fields is obvious, so that the linearity of the magnetization process of the magnetically soft alloy is poor, and the stability of the electromagnetic device to electromagnetic signal transmission is easy to cause to be reduced.
Constant magnetic alloys are a class of magnetically soft alloys having constant permeability properties, while having a low remanence level, and are commonly used in electromagnetic devices where a high linearity requirement for the magnetization process is desired. Common constant magnetic-conductive soft magnetic alloys at home and abroad are such as national standards 1J34H and 1J50H, russian 47HX and other alloys. The processing mode of the constant magnetic conduction material is to control the deformation of the cold rolled finished product, ensure that the alloy forms a cubic texture, then carry out high-temperature annealing and magnetic field heat treatment to form a preferred texture, and form the soft magnetic alloy with constant magnetic conductivity and low remanence characteristics. In addition, the deformation of the cold-rolled finished product is strictly limited in the production process of the constant magnetic alloy, so that the method is not beneficial to processing electromagnetic devices requiring the dimension specification of materials and the state of the materials to be in a hot working state.
From the above, it is known that the existing medium-nickel high-magnetic induction soft magnetic alloy cannot obtain the characteristics of constant magnetic permeability and low remanence through the conventional processing means. Therefore, aiming at the existing problems, a soft magnetic alloy with high processing efficiency, high magnetic induction and low remanence characteristic, excellent magnetic performance temperature stability and magnetic permeability constancy is required to be developed on the basis of the existing medium nickel soft magnetic alloy so as to meet the use requirements under specific conditions, and meanwhile, the existing medium nickel soft magnetic alloy series is enriched.
Disclosure of Invention
The application provides a method for preparing a medium nickel soft magnetic alloy and a preparation method thereof, which are used for solving the technical problem that the existing medium nickel soft magnetic alloy is difficult to simultaneously consider high magnetic induction performance and low remanence performance.
In a first aspect, the present application provides a medium nickel soft magnetic alloy, the alloy comprising the chemical components of:
ni, cr, nb, mn, si, C, fe; wherein,,
the content of Ni is 47.50-49.00 wt%, the content of Cr is 0.10-0.50 wt%, the content of Nb is 0.01-0.20 wt%, the content of Mn is 0.10-0.50 wt%, the content of Si is 0.05-0.30 wt%, and the content of C is less than 0.01 wt%.
Optionally, the magnetic properties of the alloy include: mu (mu) 0.005Oe ≥20mH/m，μ m More than or equal to 150mH/m, bs more than or equal to 1.60T, br less than 0.55T, hc less than 3A/m, mu within the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 20 percent.
In a second aspect, the present application provides a method for preparing a middle nickel soft magnetic alloy, which is used for preparing the alloy according to any embodiment of the first aspect, and the method includes:
under the condition of a first set temperature, performing first heating and first heat preservation on the blank, forging, and controlling the deformation ratio of the forging;
under the condition of a second set temperature, carrying out second heating and second heat preservation on the forged blank, rolling, and controlling the rolling deformation ratio;
and annealing and third heat preservation are carried out on the rolled blank under the condition of a third set temperature, and then cooling is carried out, so that the medium nickel soft magnetic alloy is obtained.
Optionally, the first set temperature is 1050-1150 ℃, and the first heat preservation time is 1-5 h.
Optionally, the second set temperature is 1050-1150 ℃, and the second heat preservation time is 1-5 h.
Optionally, the forging deformation ratio is 1.5-4.5.
Optionally, the rolling deformation ratio is 1.5-4.5.
Optionally, the third set temperature is 1050 ℃ to 1150 ℃.
Optionally, the third heat preservation time is 3h-6h.
Optionally, the cooling rate is 200 ℃/h to 500 ℃/h.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
(1) Compared with the traditional medium nickel soft magnetic alloy, the alloy has higher mu 0 、μ m And Bs and low Br, and simultaneously has excellent magnetic performance temperature stability and constant magnetic permeability, and an electromagnetic device manufactured by the electromagnetic device can meet the use requirements under certain specific conditions, thereby being beneficial to improving the response speed of the electromagnetic device, reducing the hysteresis effect of the electromagnetic device and realizing the miniaturization of the electromagnetic device; (2) The method aims at the problem that the magnetic temperature stability fluctuation of the magnetic material is large originally, and mainly ensures that the performance of the electromagnetic device does not obviously decay along with the temperature change by adding the magnetic temperature compensation alloy on the electromagnetic device. However, the temperature compensation alloy is added, so that the structure of an electromagnetic device is complicated, the miniaturization and light weight design requirements of the electromagnetic device are not met, and compared with the traditional medium nickel soft magnetic alloy, the alloy has excellent magnetic property stability, and the material can meet the use requirements in a severe temperature environment; (3) Compared with the traditional constant magnetic permeability alloy, the alloy has the advantages of short processing flow, small limitation on production equipment and processing modes and the like, and can obtain lower residual magnetism level by reasonably controlling the hot processing heating temperature, the deformation ratio, the heat treatment annealing temperature and the cooling speed, and meanwhile, the alloy has the excellent constant magnetic permeability, and the alloy has the advantages of simple processing technology, low cost and suitability for mass industrialized production.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the application and together with the description, serve to explain the principles of the application.
In order to more clearly illustrate the embodiments of the present application or the technical solutions in the prior art, the drawings that are required to be used in the description of the embodiments or the prior art will be briefly described below, and it will be obvious to those skilled in the art that other drawings can be obtained from these drawings without inventive effort.
Fig. 1 is a schematic flow chart of a method for preparing a middle nickel soft magnetic alloy according to an embodiment of the present application.
Detailed Description
For the purposes of making the objects, technical solutions and advantages of the embodiments of the present application more clear, the technical solutions of the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is apparent that the described embodiments are some embodiments of the present application, but not all embodiments. All other embodiments, which can be made by one of ordinary skill in the art without undue burden from the present disclosure, are within the scope of the present application based on the embodiments herein.
Various embodiments of the present application may exist in a range format; it should be understood that the description in a range format is merely for convenience and brevity and should not be interpreted as a rigid limitation on the scope of the application. It is therefore to be understood that the range description has specifically disclosed all possible sub-ranges and individual values within that range. For example, it should be considered that a description of a range from 1 to 6 has specifically disclosed sub-ranges, such as from 1 to 3, from 1 to 4, from 1 to 5, from 2 to 4, from 2 to 6, from 3 to 6, etc., as well as single numbers within the range, such as 1, 2, 3, 4, 5, and 6, wherever applicable. In addition, whenever a numerical range is referred to herein, it is meant to include any reference number (fractional or integer) within the indicated range.
In this application, unless otherwise indicated, terms of orientation such as "upper" and "lower" are used specifically to refer to the orientation of the drawing in the figures. In addition, in the description of the present application, the terms "include", "comprise", "comprising" and the like mean "including but not limited to". Relational terms such as "first" and "second", and the like may be used solely to distinguish one entity or action from another entity or action without necessarily requiring or implying any actual such relationship or order between such entities or actions. Herein, "and/or" describing an association relationship of an association object means that there may be three relationships, for example, a and/or B, may mean: a alone, a and B together, and B alone. Wherein A, B may be singular or plural. Herein, "at least one" means one or more, and "a plurality" means two or more. "at least one", "at least one" or the like refer to any combination of these items, including any combination of single item(s) or plural items(s). For example, "at least one (individual) of a, b, or c," or "at least one (individual) of a, b, and c," may each represent: a, b, c, a-b (i.e., a and b), a-c, b-c, or a-b-c, wherein a, b, c may be single or multiple, respectively.
Unless specifically indicated otherwise, the various raw materials, reagents, instruments, equipment, and the like used in this application are commercially available or may be prepared by existing methods.
The application provides a middle nickel soft magnetic alloy with high magnetic induction characteristic and a preparation scheme thereof aiming at the defects of the existing alloy, the alloy has lower remanence level, higher magnetic performance temperature stability and constant magnetic conduction characteristic compared with the traditional middle nickel soft magnetic alloy with high magnetic induction, and meanwhile, compared with the traditional constant magnetic conduction soft magnetic alloy processing mode, the alloy processing mode of the application has the advantages of high processing efficiency, short production flow and the like, and the high magnetic induction low remanence soft magnetic alloy processed by the mode can meet the use requirement under certain specific conditions after being applied to electromagnetic devices, and meanwhile, the application can perfect the existing middle nickel soft magnetic alloy series.
In a first aspect, the present application provides a medium nickel soft magnetic alloy, the alloy comprising the chemical components of:
ni, cr, nb, mn, si, C, fe; wherein,,
the content of Ni is 47.50-49.00 wt%, the content of Cr is 0.10-0.50 wt%, the content of Nb is 0.01-0.20 wt%, the content of Mn is 0.10-0.50 wt%, the content of Si is 0.05-0.30 wt%, and the content of C is less than 0.01 wt%.
The positive effect of controlling the Ni content to be 47.50-49.00 wt%: ensuring that the alloy obtains higher magnetic induction and magnetic conductivity. If the Ni content is too high, the alloy saturation magnetization Bs is reduced to some extent; if Ni content is too low, it will result in a certain degree of permeability 0.005Oe Mu and mu m And (3) lowering. Specifically, ni contentMay be 47.50 wt%, 48.00 wt%, 48.50 wt%, 49.00 wt%, etc.
The positive effect of controlling the Cr content to be 0.10-0.50 wt%: the corrosion resistance and the temperature stability of the alloy are improved. If the Cr content is too high, the alloy saturation magnetic induction Bs is reduced to a certain extent; if the Cr content is too low, the corrosion resistance and the temperature stability of the alloy are lowered to some extent. Specifically, the content of Cr may be 0.10 wt%, 0.20 wt%, 0.30 wt%, 0.40 wt%, 0.50 wt%, or the like.
The positive effect of controlling the Nb content to be 0.01-0.20 wt%: the hardness and the temperature stability of the alloy are improved. If the Nb content is too high, the alloy saturation magnetization Bs is reduced to a certain extent; if the Nb content is too low, the alloy hardness and temperature stability are lowered to some extent. Specifically, the content of Nb may be 0.01 wt%, 0.05 wt%, 0.10 wt%, 0.15 wt%, 0.20 wt%, and the like.
The positive effect of controlling the Mn content to be 0.10-0.50 wt%: and adjusting the magnetocrystalline anisotropy constant and magnetostriction coefficient of the alloy. If the Mn content is too high, the alloy saturation magnetization Bs is reduced to some extent; if the Mn content is too low, the magnetocrystalline anisotropy constant and magnetostriction coefficient are too large to a certain extent, the dependence on the cooling speed in the alloy heat treatment process is improved, and the magnetic permeability mu of the alloy is reduced 0.005Oe Mu and mu m . Specifically, the content of Mn may be 0.10 wt%, 0.20 wt%, 0.30 wt%, 0.40 wt%, 0.50 wt%, or the like.
The positive effect of controlling the Si content to be 0.05-0.30 wt%: and the alloy is combined with impurity elements such as O element, so that the content of alloy gas elements is reduced, and the purity of the alloy is improved. If the Si content is too high, the alloy saturation magnetic induction Bs is reduced to a certain extent; if the Si content is too low, the purity of the alloy is reduced to a certain extent, and the magnetic permeability mu of the alloy is caused 0.005Oe Mu and mu m The coercivity Hc is improved while the coercivity is reduced. Specifically, the content of Si may be 0.10 wt%, 0.20 wt%, 0.30 wt%, 0.40 wt%, 0.50 wt%, or the like。
Positive effect of controlling the content of C to < 0.01 wt.%: and the alloy is combined with impurity elements such as O, N and the like, so that the content of the alloy gas element is reduced, and the purity of the alloy is improved. If the content of C is too high, the purity of the alloy is reduced to a certain extent, so that the magnetic permeability mu of the alloy is reduced 0.005Oe Mu and mu m The coercivity Hc is improved while the coercivity is reduced. Specifically, the content of C may be 0.009 wt%, 0.0095 wt%, 0.008 wt%, 0.0085 wt%, or the like.
In some embodiments, the magnetic properties of the alloy include: mu (mu) 0.005Oe ≥20mH/m，μ m More than or equal to 150mH/m, bs more than or equal to 1.60T, br less than 0.55T, hc less than 3A/m, mu within the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 20 percent.
The alloy in the embodiment of the application meets the magnetic performance, and the medium nickel soft magnetic alloy can simultaneously give consideration to high magnetic induction performance and low remanence performance. Specific alloy properties can be seen in examples 1-7.
In a second aspect, the present application provides a method for preparing a nickel-in-nickel soft magnetic alloy to implement the alloy according to any one of the embodiments of the first aspect, referring to fig. 1, the method includes:
s1, under the condition of a first set temperature, performing first heating and first heat preservation on a blank, forging, and controlling the deformation ratio of the forging;
s2, under the condition of a second set temperature, carrying out second heating and second heat preservation on the forged blank, rolling, and controlling the rolling deformation ratio;
and S3, annealing and third heat preservation are carried out on the rolled blank under the condition of a third set temperature, and then cooling is carried out, so that the medium nickel soft magnetic alloy is obtained.
The alloy processing mode has the advantages of high processing efficiency, short production flow and the like, and the high-magnetic-induction low-remanence soft magnetic alloy processed by the mode can meet the use requirements under certain specific conditions after being applied to electromagnetic devices, and can be used for perfecting the traditional medium-nickel soft magnetic alloy series. Before the step S1 is executed, the alloy is subjected to vacuum smelting to obtain a blank.
In some embodiments, the first set temperature is 1050 ℃ to 1150 ℃ and the first incubation time is 1h to 5h.
"first set temperature" means the temperature of the first heating, and the positive effect of controlling the first set temperature to 1050 ℃ -1150 ℃: ensuring that the alloy has a uniform grain size. If the temperature is too high, abnormal growth of crystal grains can be caused to a certain extent, so that the remanence Br of the alloy after heat treatment is obviously improved; if the temperature is too low, grains cannot sufficiently grow up to a certain extent, so that the magnetic permeability of the alloy after heat treatment is too low. Specifically, the heating temperature for forging may be 1050 ℃, 1070 ℃, 1090 ℃, 1110 ℃, 1130 ℃, 1150 ℃, or the like.
The first heat preservation means heat preservation treatment after the blank is provided with a first heat preservation temperature under the condition of the first heating temperature, the first heat preservation temperature is the same as the first heating temperature in value, and the positive effect of controlling the first heat preservation time to be 1h-5h is that: ensuring that the alloy has a uniform grain size. If the time is too long, abnormal growth of crystal grains can be caused to a certain extent, so that the remanence Br of the alloy after heat treatment is obviously improved; if the time is too short, grains cannot sufficiently grow up to a certain extent, and the magnetic permeability of the alloy after heat treatment is too low. Specifically, the incubation time may be 1h, 2h, 3h, 4h, 5h, etc.
In some embodiments, the second set temperature is 1050 ℃ to 1150 ℃ and the second incubation time is 1h to 5h.
"second set temperature" means the temperature of the second heating, and the positive effect of controlling the second set temperature to 1050 ℃ -1150 ℃: ensuring that the alloy has a uniform grain size. If the temperature is too high, abnormal growth of crystal grains can be caused to a certain extent, so that the remanence Br of the alloy after heat treatment is obviously improved; if the temperature is too low, grains cannot sufficiently grow up to a certain extent, so that the magnetic permeability of the alloy after heat treatment is too low. Specifically, the heating temperature of the hot rolling may be 1050 ℃, 1070 ℃, 1090 ℃, 1110 ℃, 1130 ℃, 1150 ℃, or the like.
The second heat preservation means heat preservation treatment after the blank is provided with the second heat preservation temperature under the condition of the second heating temperature, the second heat preservation temperature is the same as the second heating temperature in value, and the positive effect of controlling the second heat preservation time to be 1h-5h is that: ensuring that the alloy has a uniform grain size. If the time is too long, abnormal growth of crystal grains can be caused to a certain extent, so that the remanence Br of the alloy after heat treatment is obviously improved; if the time is too short, grains cannot sufficiently grow up to a certain extent, and the magnetic permeability of the alloy after heat treatment is too low. Specifically, the incubation time may be 1h, 2h, 3h, 4h, 5h, etc.
In some embodiments, the forging has a deformation ratio of 1.5 to 4.5.
In some embodiments, the rolling has a deformation ratio of 1.5 to 4.5.
The positive effect of controlling the forging deformation ratio and rolling deformation ratio to be 1.5-4.5: ensuring that the alloy forms a preferred orientation for magnetization. If the deformation ratio is too high, the alloy remanence Br is too high to a certain extent; if the deformation ratio is too low, the alloy cannot form preferred orientation favorable for magnetization to a certain extent, resulting in magnetic permeability mu 0.005Oe Mu and mu m And (3) lowering. Specifically, the forging and rolling deformation ratio may be 1.5, 2, 2.5, 3, 3.5, 4, 4.5, or the like.
In some embodiments, the third set temperature is 1050 ℃ to 1150 ℃.
The "third set temperature" means an annealing temperature, which is annealed by a hood-type furnace in the embodiment of the present application, and the annealing atmosphere is H 2 The positive effect of controlling the second set temperature to 1050-1150 ℃ is that: ensuring that the alloy attains the appropriate grain size. If the temperature is too high, abnormal growth of crystal grains can be caused to a certain extent, so that the remanence Br of the alloy is increased; if the temperature is too low, the permeability mu is caused to some extent 0.005Oe Mu and mu m Decreasing and coercive force Hc increasing. Specifically, the annealing temperature may be 1050, 1070 ℃, 1090 ℃, 1110 ℃, 1130 ℃, 1150 ℃, or the like.
In some embodiments, the third incubation time is 3h to 6h.
The third heat preservation means heat preservation treatment after the blank has a third heat preservation temperature under the condition of the annealing temperature, the third heat preservation temperature is the same as the annealing temperature in value, and the positive effect of controlling the third heat preservation time to be 3-6 h is that: ensuring that the alloy attains the appropriate grain size. If the time is too long, abnormal growth of crystal grains can be caused to a certain extent, so that the remanence Br of the alloy is increased; if the time is too short, the permeability μmay be caused to some extent 0.005Oe Mu and mu m Decreasing and coercive force Hc increasing. Specifically, the incubation time may be 3h, 4h, 5h, 6h, etc.
In some embodiments, the cooling is at a rate of 200 ℃/h to 500 ℃/h.
The positive effect of controlling the cooling speed to be 200 ℃/h to 500 ℃/h: ensuring that the alloy has lower magnetocrystalline anisotropy constant and thermal stress sensitivity. If the cooling speed is too high, the alloy thermal stress is too high to a certain extent, and the magnetic permeability mu is reduced 0.005Oe Mu and mu m The coercive force Hc is improved; if the cooling speed is too low, the magnetocrystalline anisotropy constant is increased to a certain extent, and the magnetic permeability mu is reduced 0.005Oe Mu and mu m The coercive force Hc is improved. Specifically, the cooling rate may be 200 ℃/h, 300 ℃/h, 400 ℃/h, 500 ℃/h, or the like.
The middle nickel soft magnetic alloy is realized based on the preparation method of the middle nickel soft magnetic alloy, and specific steps of the preparation method of the middle nickel soft magnetic alloy can refer to the embodiment, and as the middle nickel soft magnetic alloy adopts part or all of the technical schemes of the embodiment, the middle nickel soft magnetic alloy has at least all the beneficial effects brought by the technical schemes of the embodiment, and the detailed description is omitted.
The application solves the technical problem that the existing medium nickel soft magnetic alloy is difficult to simultaneously consider high magnetic induction performance and low remanence performance, and the magnetic performance of the alloy comprises: mu (mu) 0.005Oe ≥20mH/m，μ m More than or equal to 150mH/m, bs more than or equal to 1.60T, br less than 0.55T, hc less than 3A/m. Meanwhile, the alloy disclosed by the application has certain constant magnetic permeability characteristic and the preparation method thereofCompared with the traditional constant magnetic alloy processing and preparing method, the method has the advantages of short processing flow, small limitation on production equipment and processing modes and the like, and by reasonably controlling the heating temperature, the deformation ratio, the annealing temperature and the cooling speed of the heat treatment, the alloy can obtain the constant magnetic conductivity characteristic, and simultaneously has excellent magnetic performance temperature stability and low remanence characteristic, and mu in the temperature range of-120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the electromagnetic device in the magnetic field of 0.5 Oe-20 Oe is not more than 20%, so that the electromagnetic device has higher linearity in the magnetizing process, and meets the use requirement of the electromagnetic device in a complex temperature environment. The alloy is suitable for mass industrialized production.
The present application is further illustrated below in conjunction with specific examples. It should be understood that these examples are illustrative only of the present application and are not intended to limit the scope of the present application. The experimental procedures, which are not specified in the following examples, are generally determined according to national standards. If the corresponding national standard does not exist, the method is carried out according to the general international standard, the conventional condition or the condition recommended by the manufacturer.
Example 1: the alloy comprises the following chemical components in percentage by mass: nickel: 47.65; chromium: 0.10; niobium: 0.01; manganese: 0.10; silicon: 0.10; carbon: 0.0095; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank;
under the condition of 1150 ℃, carrying out first heating and first heat preservation on the blank for 1h, forging, and controlling the deformation ratio of the forging to be 4.0; under the condition of 1150 ℃, carrying out second heating and second heat preservation on the forged blank for 1h, then rolling, and controlling the deformation ratio of the rolling to be 4.0; the annealing temperature of the heat treatment is 1150 ℃, the annealing heat preservation time is 3 hours, the heat treatment is followed by cooling to room temperature at a cooling rate of 300 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝25mH/m，μ m =165 mH/m, bs=1.65t, br=0.58t, hc=1.5A/m. Mu in the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m 10% of the total magnetic permeability, and the magnetic permeability stability alpha under the magnetic field of 0.5 Oe-20 Oe is not more than20％。
Example 2: the alloy comprises the following chemical components in percentage by mass: nickel: 47.85; chromium: 0.10; niobium: 0.02; manganese: 0.20; silicon: 0.15; carbon: 0.009; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank;
heating the blank for 3 hours at 1130 ℃ and preserving heat for the first time, forging, and controlling the deformation ratio of the forging to be 3.5; under the condition of 1130 ℃, carrying out second heating and second heat preservation on the forged blank for 3 hours, then rolling, and controlling the deformation ratio of the rolling to be 3.5; the annealing temperature of the heat treatment is 1120 ℃, the annealing heat preservation time is 4 hours, the heat treatment is carried out, the heat treatment is cooled to room temperature at the cooling speed of 300 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝22.5mH/m，μ m =155 mH/m, bs=1.63 t, br=0.55 t, hc=2.0A/m. Mu in the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 20 percent.
Example 3: the alloy comprises the following chemical components in percentage by mass: nickel: 48.05; chromium: 0.15; niobium: 0.05; manganese: 0.25; silicon: 0.20; carbon: 0.008; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank; under the condition of 1100 ℃, performing first heating and first heat preservation on the blank for 5 hours, forging, and controlling the deformation ratio of the forging to be 3.0; under 1100 ℃, carrying out second heating and second heat preservation on the forged blank for 5 hours, then rolling, and controlling the deformation ratio of the rolling to be 3.0; the annealing temperature of the heat treatment is 1100 ℃, the annealing heat preservation time is 5 hours, the heat treatment is carried out, the heat treatment is cooled to room temperature at a cooling speed of 400 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝22.5mH/m，μ m =155 mH/m, bs=1.61 t, br=0.52t, hc=2.3A/m. Mu m fluctuation range within the temperature range of 120 ℃ below zero to 120 ℃ below zero not exceeding room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 15 percent.
Example 4: the alloy comprises the following chemical components in percentage by mass: nickel: 48.25; chromium: 0.15; niobium: 0.05; manganese: 0.35; silicon: 0.25; carbon: 0.0085; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank;
under the condition of 1150 ℃, the blank is subjected to first heating and first heat preservation for 4 hours, then is forged, and the deformation ratio of the forging is controlled to be 3.5; under the condition of 1150 ℃, carrying out second heating and second heat preservation on the forged blank for 4 hours, then rolling, and controlling the deformation ratio of the rolling to be 3.5; the annealing temperature of the heat treatment is 1150 ℃, the annealing heat preservation time is 5 hours, the heat treatment is followed by cooling to room temperature at a cooling rate of 400 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝22mH/m，μ m =150 mH/m, bs=1.60 t, br=0.50 t, hc=2.5A/m. The fluctuation range of mu m in the temperature range of 120 ℃ to 120 ℃ is not more than +/-6% of mu m at room temperature, and the magnetic permeability stability alpha under the magnetic field of 0.5Oe to 20Oe is not more than 15%.
Example 5: the alloy comprises the following chemical components in percentage by mass: nickel: 48.75; chromium: 0.25; niobium: 0.05; manganese: 0.30; silicon: 0.20; carbon: 0.0085; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank;
first heating and first heat preservation are carried out on the blank for 4 hours under the condition of 1050 ℃, then forging is carried out, and the deformation ratio of the forging is controlled to be 2.5; under 1100 ℃, carrying out second heating and second heat preservation on the forged blank for 4 hours, then rolling, and controlling the deformation ratio of the rolling to be 2.5; the annealing temperature of the heat treatment is 1100 ℃, the annealing heat preservation time is 5 hours, the heat treatment is carried out, the heat treatment is cooled to room temperature at a cooling speed of 400 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝20mH/m，μ m =150 mH/m, bs=1.60 t, br=0.45 t, hc=2.8A/m. Mu in the temperature range of-120 ℃ to 120 DEG C m The fluctuation range of the magnetic field is not more than +/-6% of mu m at room temperature, and the magnetic permeability stability alpha under the magnetic field of 0.5 Oe-20 Oe is not more than 12%.
Example 6: the alloy comprises the following chemical components in percentage by mass: nickel: 48.95; chromium: 0.28; niobium: 0.18; manganese: 0.15; silicon: 0.10; carbon: 0.0080; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank;
under the condition of 1150 ℃, carrying out first heating and first heat preservation on the blank for 3 hours, forging, and controlling the deformation ratio of the forging to be 4.0; under the condition of 1150 ℃, carrying out second heating and second heat preservation on the forged blank for 3 hours, then rolling, and controlling the deformation ratio of the rolling to be 4.0; the annealing temperature of the heat treatment is 1150 ℃, the annealing heat preservation time is 6 hours, the heat treatment is followed by cooling to room temperature at a cooling rate of 500 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝22.5mH/m，μ m =165 mH/m, bs=1.60 t, br=0.55 t, hc=2.2A/m. Mu m fluctuation range within the temperature range of 120 ℃ below zero to 120 ℃ below zero not exceeding room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 15 percent.
Example 7: the alloy comprises the following chemical components in percentage by mass: nickel: 47.55; chromium: 0.20; niobium: 0.05; manganese: 0.15; silicon: 0.05; carbon: < 0.01; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank;
under the condition of 1150 ℃, the blank is subjected to first heating and first heat preservation for 4 hours, then is forged, and the deformation ratio of the forging is controlled to be 4.0; under 1100 ℃, carrying out second heating and second heat preservation on the forged blank for 4 hours, then rolling, and controlling the deformation ratio of the rolling to be 4.0; the annealing temperature of the heat treatment is 1150 ℃, the annealing heat preservation time is 5 hours, the heat treatment is followed by cooling to room temperature at a cooling rate of 300 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝28mH/m，μ m =170 mH/m, bs=1.67 t, br=0.58 t, hc=2.95A/m. Mu in the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 20 percent.
Comparative example 1:
the alloy comprises the following chemical components in percentage by mass: nickel: 49.50; chromium: 0; niobium: 0; manganese: 0.50; silicon: 0.25; carbon: 0.01; the balance being iron and unavoidable impurities. Smelting by adopting a vacuum induction furnace to obtain a blank; heating the blank for 5h at 1180deg.C, forgingControlling the deformation ratio of the forging to be 1.3; under the condition of 1180 ℃, carrying out second heating and second heat preservation on the forged blank for 5 hours, then rolling, and controlling the deformation ratio of the rolling to be 1.3; the annealing temperature of the heat treatment is 1180 ℃, the annealing heat preservation time is 6 hours, the heat treatment is carried out, the heat treatment is cooled to room temperature at the cooling speed of 600 ℃/h, and the magnetic properties of the alloy are as follows: mu (mu) 0.005Oe ＝(10)mH/m，μ m =85 mH/m, bs=1.53 t, br=0.70 t, hc=4.5A/m. Mu in the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 50 percent.
Through the specific embodiments of examples 1-7, the prepared medium nickel soft magnetic alloy has excellent performance by optimizing the alloy component proportion and reasonably controlling the hot working process parameters and the heat treatment process parameters, and can simultaneously realize high magnetic induction performance and low remanence performance, and the prepared alloy of comparative example 1 has far lower performance than the alloy of the example.
The foregoing is merely a specific embodiment of the application to enable one skilled in the art to understand or practice the application. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the application. Thus, the present application is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (10)
1. A medium nickel soft magnetic alloy, characterized in that the alloy comprises the following chemical components:
ni, cr, nb, mn, si, C, fe; wherein,,
the content of Ni is 47.50-49.00 wt%, the content of Cr is 0.10-0.50 wt%, the content of Nb is 0.01-0.20 wt%, the content of Mn is 0.10-0.50 wt%, the content of Si is 0.05-0.30 wt%, and the content of C is less than 0.01 wt%.
2. The alloy of claim 1, wherein the magnetic properties of the alloy comprise: mu (mu) 0.005Oe ≥20mH/m，μ m More than or equal to 150mH/m, bs more than or equal to 1.60T, br less than 0.55T, hc less than 3A/m, mu within the temperature range of-120 ℃ to 120 DEG C m Mu when the fluctuation range of (C) is not more than room temperature m The magnetic permeability stability alpha of the magnetic field of 0.5 Oe-20 Oe is not more than 20 percent.
3. A method for preparing a medium nickel soft magnetic alloy, for preparing the alloy of claim 1 or 2, comprising:
under the condition of a first set temperature, performing first heating and first heat preservation on the blank, forging, and controlling the deformation ratio of the forging;
under the condition of a second set temperature, carrying out second heating and second heat preservation on the forged blank, rolling, and controlling the rolling deformation ratio;
and annealing and third heat preservation are carried out on the rolled blank under the condition of a third set temperature, and then cooling is carried out, so that the medium nickel soft magnetic alloy is obtained.
4. A method according to claim 3, wherein the first set temperature is 1050-1150 ℃ and the first incubation time is 1-5 h.
5. A method according to claim 3, wherein the second set temperature is 1050-1150 ℃ and the second incubation time is 1-5 h.
6. A method according to claim 3, wherein the forging deformation ratio is 1.5-4.5.
7. A method according to claim 3, characterized in that the rolling deformation ratio is 1.5-4.5.
8. A method according to claim 3, wherein the third set temperature is 1050-1150 ℃.
9. A method according to claim 3, wherein the third incubation time is 3h to 6h.
10. A method according to claim 3, wherein the cooling is at a rate of 200 ℃/h to 500 ℃/h.
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