CN103114234A - Alloy with excellent room-temperature soft magnetic property and mechanical property, and preparation method thereof - Google Patents
Alloy with excellent room-temperature soft magnetic property and mechanical property, and preparation method thereof Download PDFInfo
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Abstract
The invention discloses alloy with excellent room-temperature soft magnetic property and mechanical property, and a preparation method thereof, and belongs to the technical field of soft magnetic alloy, wherein the alloy is Fe-49Co-2V-xCr, wherein x is smaller than or equal to 1.0 and greater than 0, and is atomic percent; preferably x is smaller than 0.5 and greater than 0; the preparation method comprises the steps of smelting, vacuum diffusing and annealing, high-temperature forging, hot rolling, cold rolling and final heat treatment. The FeCoVCr alloy provided by the invention is excellent in room-temperature mechanical property; the tensile strength can be up to 912MPa; the elongation can be up to 10.9%; the alloy has soft magnetic property; and the coercivity does not exceed 3.58Oe. The alloy is simple in preparation technology, and a large-sized alloy material can be prepared conveniently.
Description
Technical field
The present invention relates to the non-retentive alloy technical field, relate in particular to a kind of high saturated magnetic induction, low-coercivity, high room temperature strength, good (crystalline state) non-retentive alloy and the technology of preparing thereof of plasticity.
Background technology
Soft magnetic materials because of its can be under the condition that adds a low-intensity magnetic field magnetization easily, so consisted of an engineering materials very important branch.Usually, the characteristics of non-retentive alloy are high initial magnetization intensity and low-coercivity.Their magnetic property is to have determined its application, comprises generating, distribution, solenoid coil, magnetic shielding, data storage and microwave communication.In soft magnetic materials, electronic sheet material is comparatively leading on share of market.FeCo base non-retentive alloy is because having the characteristics such as high saturation and magnetic intensity, high-curie temperature, low magnetocrystalline anisotropy and high strength, become the ideal material of high magnetic flux density product, be widely used in fields such as Aeronautics and Astronautics, navigation, military and civilians.At present, the FeCo alloy is having greater advantage due to its high saturation and magnetic intensity aspect part loss of weight or volume of part reduction, for example, replaces the Fe-Si alloy can alleviate the quality of 20-25% with the FeCo alloy.
In recent years, on the basis of Fe-Co alloy, Fe-Co-V non-retentive alloy, Fe-Co base amorphous and Fe-Co base nanometer crystal material have been developed.Yet, although the soft magnetism excellent performance of amorphous and nano crystal soft magnetic material is awaiting breakthrough aspect the gordian techniquies such as preparation large-size alloy material and its high-temperature stability.At present, still be in the laboratory study stage.
Add V to improve the alloy cold-workability in traditional F eCo alloy, also have report to show, adding of V can be carried heavy alloyed resistance, effectively reduces the loss in use procedure.The external FeCo alloy of having studied and produced some trades mark comprises Permendur, 2V-Pemendur, Hiperco, Supermendur etc.Wherein the coercive force of Permendur alloy is 0.2Oe, and saturation magnetization is 2.4T, and tensile strength is 600MPa, but unit elongation is only 2%, in actual production is used, certain restriction is arranged.
The U.S. proposes the how electric aircraft of development a new generation from the nineties in last century, and namely " More Electric Aircraft(MEA) ", Material Field is more obvious in the progress that is applicable to the aviation concerned power.Many electric aircrafts adopt the different subsystem of driven by power, and due to the driving of electric power, time and oil consumption that aircraft arrives cruising altitude are reduced, and reliability, the maintainability of aircraft improve greatly, and have reduced the demand to ground support system.Some gordian techniquies wherein, comprehensive electric generating unit for example, promote mainly internal triggering machine/generator and magnetic bearing system into engine, need to satisfy the soft magnetic materials of high-temperature service condition, these requirements are included in has higher magnetic induction density (〉 2T between 500-600 ℃ of temperature), good mechanical stability (〉 5000h), and during 5kHz less than 480W kg
-1Core loss.FeCo base alloy naturally becomes good suitable material.But the mechanical property of FeCo base alloy can't satisfy requirement of strength design at present.
Simultaneously, along with increasing of frequency of utilization, because the resistivity of metal soft magnetic material is lower, can cause large eddy-current loss, can cause skin effect under higher frequency, this has just seriously limited the application of the high band of FeCo base alloy.For this reason, the resistivity that improves under the alloy high frequency also becomes one of research direction of FeCo base non-retentive alloy.
China Fe-Co magnetically soft alloy has 1J20,1J21, three kinds of trades mark of 1J22 now, and has formed the heat treating regime of regulation.Wherein 1J21,1J22 are comparatively commonly used, are equivalent to external 2V-Permendur alloy.The 1J22 alloy is widely used in the aviation that requirement is lightweight, volume is little at present, is also the non-retentive alloy the most widely that China is applied to aerogenerator at present, but at present ubiquity magnetic performance and mechanical property can't compatibility etc. problem, material plasticity is relatively poor.
In order to satisfy the domestic application demand, also carry out place mat for the research of high temperature non-retentive alloy, obtain the FeCoV base non-retentive alloy that soft magnetic performance excellence and mechanical property are taken into account, have great importance.
Summary of the invention
The present invention for solve existing FeCoV base non-retentive alloy soft magnetic performance and mechanical property can not fine compatibility problem, a kind of FeCoVCr Alloy And Preparation Method is provided.Described FeCoVCr base non-retentive alloy is Fe-49Co-2V-xCr, and wherein 0＜x≤1.0, more than be atomic percent, preferred 0＜x＜0.5.Less than below 3.58Oe, tensile strength is greater than 507MPa through the coercive force that obtains alloy after 800～850 ℃ of final thermal treatment temps for described non-retentive alloy, and unit elongation is greater than 4.4%.In described non-retentive alloy microstructure, separate out at the grain boundaries particle that is magnetic, precipitated phase particle size 0.3～1.2 μ m, percent by volume is 5～16%.
The present invention also provides a kind of preparation method of above-mentioned FeCoVCr base non-retentive alloy, and concrete steps are as follows:
The first step is carried out the proportioning melting with raw material, and the melting mode is vacuum arc furnace melting;
Second step, vacuum diffusion annealing, temperature 〉=900 ℃, annealing time 2～10h, melted ingot furnace cooling;
The 3rd step, high temperature forging; Forging temperature is higher than 800 ℃;
The 4th step is to forging bulk through the hot rolling of the continuous three above passages of passage;
In the 5th step, alloy carries out cold rolling processing sheet material, sheet material, deflection 10～95%;
In the 6th step, alloy carries out final thermal treatment, and temperature is 350～980 ℃, and heat treatment time is 2h, and the type of cooling is air cooling.
The invention has the advantages that:
(1) FeCoVCr Alloy At Room Temperature good mechanical performance provided by the invention, tensile strength is up to 912MPa, and unit elongation reaches 10.9%, and soft magnetic performance is taken into account, and coercive force is no more than 3.58Oe.
(2) non-retentive alloy preparation technology provided by the invention is simple, is convenient to prepare the large-size alloy material.
Description of drawings
Fig. 1 is the EPMA(electronic probe after the final thermal treatment of Fe-49Co-2V-xCr (x=0,0.3,0.5,0.7) alloy) photo (BEI backscattered electron phase); (a) x=0, (b) x=0.3, (c) x=0.5, (d) x=0.7;
Fig. 2 is the metallograph after the final thermal treatment of Fe-49Co-2V-0.5Cr alloy;
Fig. 3 is the stretching fracture photo of Fe-49Co-2V-0.7Cr alloy after the final thermal treatment temp of difference is processed;
Fig. 4 is the coercive force curve of Fe-49Co-2V-xCr after cold rolling attitude and heat treatments at different (x=0,0.3,0.5,0.7,1.0) alloy;
The tensile strength curve of Fe-49Co-2V-xCr after the cold rolling attitude of Fig. 5 and heat treatments at different (x=0,0.3,0.5,0.7,1.0) alloy;
The unit elongation curve of Fe-49Co-2V-xCr after the cold rolling attitude of Fig. 6 and heat treatments at different (x=0,0.3,0.5,0.7,1.0) alloy.
Embodiment
The present invention is described in detail below in conjunction with drawings and Examples.
The invention provides a kind of Fe-49Co-2V-xCr alloy, 0＜x≤1.0 more than are atomic percent.Preferably, 0＜x＜0.5, more preferably 0＜x＜0.3.Described FeCoVCr alloy has good comprehensive mechanical property and soft magnetic performance, and tensile strength reaches 912MPa, and unit elongation reaches 10.9%, and soft magnetic performance is taken into account, and coercive force is less than 3.58Oe.Above-mentioned alloy is carried out the Analysis on Microstructure particle of finding to be magnetic separate out on the crystal boundary of alloy structure, and precipitated phase particle size 0.3～1.2 μ m, percent by volume is 5～16%.
The present invention also provides a kind of preparation method of described FeCoVCr non-retentive alloy, and concrete steps are:
The first step is chosen raw material and is carried out the proportioning melting, and the melting mode is vacuum arc furnace melting, argon shield.Described proportioning raw materials is Fe-49Co-2V-xCr, and 0＜x≤1.0 more than are atomic percent.
Second step carries out vacuum diffusion annealing to alloy after melting, temperature 〉=900 ℃, annealing time 2～10h, melted ingot furnace cooling.
In the 3rd step, high temperature forging by forging the defective such as loose can eliminate that alloy produces in fusion process, is optimized heterogeneous microstructure.High temperature forging temperature 〉=800 ℃.
In the 4th step, with the hot rolling more than continuous three passages of bulk process that obtain after the 3rd step high temperature forging, hot rolling must be carried out after 1000 ℃ of insulation 1h.By high temperature forging and hot rolling, can destroy the texture of coarse crystal of alloy casting attitude, eliminate the microstructure defective, make alloy change Deformation structure into by as-cast structure, improve its processing characteristics, process industrial art performance improves.
In the 5th step, alloy carries out cold rolling, and processing becomes sheet material or sheet material, alloy deformation amount 10～95%.
In the 6th step, cold rolling rear alloy is carried out final thermal treatment.Described final thermal treatment temp is 350～980 ℃, is preferably 760～850 ℃.Heat treatment time is 2h, and the type of cooling is air cooling.
Through the non-retentive alloy that above-mentioned preparation method obtains, grain-size 15～20 μ m in alloy, crystal boundary has obvious precipitated phase, and intracrystalline also has a small amount of tiny precipitated phase (size 0.3～1.2 μ m), distributes at crystal boundary more, and intracrystalline exists on a small quantity.Determine through composition, there is the enrichment of V and Cr in precipitated phase.By the generation of precipitated phase, crystal grain is compared with matrix alloy and has been produced thinning effect.
Embodiment 1
Adopt preparation method provided by the invention to prepare the Fe-49Co-2V-0.5Cr alloy, concrete steps are as follows:
The first step, proportioning raw materials, melting.
Get purity and be 99.99% Fe and purity and be 99.9% Co, V, Cr according to atomic percent Fe-49Co-2V-0.5Cr proportioning, carry out arc melting through argon shield.For guaranteeing homogenizing, raw material is through 5 remeltings, and mass loss can be ignored.
Second step, annealing.
After 1200 ℃ of temperature of vacuum are carried out 4h diffusion annealing, the alloy furnace cooling.
The 3rd step, high temperature forging.
Melted ingot after annealing is forged, and forging temperature is 1150 ℃, alloy cube matherial thickness 6mm after forging.
The 4th step, hot rolling.
Bulk in the 3rd step after 1000 ℃ of lower alloy insulation 1h, is hot-rolled down to the thickness of 2.6mm.
In the 5th step, alloy carries out intermediate heat treatment, and condition is 750～970 ℃, 〉=10min.
The 6th step, carry out deflection and be 30% cold rolling processing, obtain the alloy sheet material.
The 7th step, final thermal treatment.
Cold rolling alloy sheet material is carried out the vacuum heat treatment of 2h differing temps, thermal treatment temp is 550 ℃, 600 ℃, 670 ℃, 760 ℃, 800 ℃, 850 ℃, 10 ℃/min of temperature rise rate, and the type of cooling is air cooling; Obtain the Fe-49Co-2V-0.5Cr non-retentive alloy of the present invention under different final thermal treatment temps.
At last Fe-49Co-2V-0.5Cr non-retentive alloy line is cut into test block, the performance of Fe-49Co-2V-0.5Cr and the performance of Fe-49Co-2V compare, the coercive force that the invention provides alloy is down to ℃ final thermal treatment of 2.6Oe(0.5Cr alloy 800), tensile strength reaches 912MPa simultaneously, unit elongation 10.9%, keeping the coercitive while preferably, improving the mechanical property of alloy.
Cold rolling attitude alloy sheet material fracture in the 5th step is analyzed, and Alloy Fracture is typical dimple pattern, and toughness is better, but because internal microstructure is rolling structure, coercive force is higher.Alloy after the 6th final thermal treatment of step is analyzed, and along with the rising of final heat treated thermal treatment temp, the Alloy Fracture pattern changes from cleavage fracture the cleavage feature that is as the criterion, and alloy plasticity improves.Fig. 2 is the metallograph of alloy after the different final thermal treatment temps of embodiment 1 alloy product are processed, and adopts the digital metaloscope of optics (Olympus BX51M) to take.Metallographic structure shows the final thermal treatment temp higher than 760 ℃, and the alloy rolling tissue is eliminated, and reply and the recrystallize of alloy are completed, and grain morphology is obvious.
Under same condition, when adopting final heat-treatment temperature range to be 760 ℃～850 ℃ to the Fe-49Co-2V matrix alloy, as shown in Fig. 1 (c), matrix alloy is along with final thermal treatment temp raises, grain growth is obvious, and grain-size increases to 40 μ m from 25 μ m, forms without precipitated phase.And after adding 0.5%Cr, formed small (0.3～1.2 μ m) precipitated phase, although intracrystalline also has precipitated phase to form, crystal boundary is separated out more obvious.Grain boundaries small size precipitated phase has hindered growing up of crystal grain effectively, and alloy grain size control corresponding to 800 ℃ of final thermal treatment is at average grain size 30 μ m after 15～20 μ m(matrix alloy uniform temp thermal treatments).Precipitated phase particle size 0.3～1.2 μ m, percent by volume is 12%.The refinement of crystal grain has improved intensity and the plasticity of alloy effectively.On the other hand, the tem analysis result of precipitated phase shows, comprise many small sizes (near nano level) particle in precipitated phase, and precipitated phase is magnetic particle, the resistance that domain wall is moved is less, grain-size reduce also deficiency so that coercive force is uprushed, therefore the present invention has obtained the non-retentive alloy that soft magnetic performance is good and mechanical property is taken into account.Electron probe microanalysis shows the result of precipitated phase research, and in precipitated phase, V and Cr content are higher than the V in matrix phase, Cr content, and as seen, Cr adds the formation that is conducive to precipitated phase.The performance data of the Fe-49Co-2V-0.5Cr alloy for preparing for the present invention as following table 1.
Table 1Fe-49Co-2V-0.5Cr alloy property
Table 1 data show, after adding the Cr element in matrix alloy Fe-49Co-2V, the raising of final thermal treatment temp is conducive to the soft magnetic performance of alloy and the comprehensive maintenance of mechanical property, especially final thermal treatment temp is 760 ℃～800 ℃, alloy coercive force 1.97Oe～2.60Oe, tensile strength 824MPa～912MPa, unit elongation 9.8%～10.9% has obtained the Fe-49Co-2V-0.5Cr non-retentive alloy of better soft magnetic performance and comprehensive mechanical property.
Embodiment 2
Employing the invention provides method and prepares the Fe-49Co-2V-0.3Cr magnetically soft alloy material, and the concrete technology step is as follows:
Purity be 99.99% Fe and purity be 99.9% Co, V, Cr according to atomic percent Fe-49Co-2V-0.3Cr proportioning, carry out arc melting through argon shield.For guaranteeing homogenizing, raw material is through 5 remeltings, and mass loss can be ignored.Then, after 1200 ℃, vacuum is carried out 4h diffusion annealing, the alloy furnace cooling.Afterwards, melted ingot is forged, forging temperature is 1150 ℃, the thickness 10mm after forging.Be hot-rolled down to 3mm after insulation 1h under 1000 ℃ afterwards.Carry out afterwards deflection and be 30% cold rolling processing.With the final thermal treatment of vacuum that cold rolling alloy sheet material carries out the 2h differing temps, final thermal treatment temp is respectively 550 ℃, 600 ℃, 670 ℃, 760 ℃, 800 ℃ and 850 ℃, 10 ℃/min of temperature rise rate, and the type of cooling is air cooling.Last line is cut into test block, and test block is carried out performance test, and test result is as shown in table 2.
Table 2Fe-49Co-2V-0.3Cr alloy performance test result
Test result shows, adding atomic percent in matrix alloy is after 0.3%Cr, as Fig. 1 (b), 800 ℃ of final thermal treatments of high temperature (〉) after formed small precipitated phase in alloy structure, crystal boundary is separated out comparatively obvious.With compare without the matrix alloy of separating out, grain boundaries small size precipitated phase has hindered growing up of crystal grain, alloy grain size control corresponding to 850 ℃ of final thermal treatment is in 18～30 μ m.Compare with matrix alloy, the refinement of crystal grain has improved intensity and the plasticity of alloy effectively.Table 2 data show, after adding the 0.3%Cr element in matrix alloy Fe-49Co-2V, the raising of final thermal treatment temp is conducive to the soft magnetic performance of alloy and the comprehensive maintenance of mechanical property, especially final thermal treatment temp is 800 ℃～850 ℃, alloy coercive force 0.63Oe～3.58Oe, tensile strength 507MPa～868MPa, unit elongation 4.4%～8.3% has obtained the Fe-49Co-2V-0.3Cr non-retentive alloy of better soft magnetic performance and comprehensive mechanical property.Compare with the Fe-49Co-2V-0.5Cr non-retentive alloy, the soft magnetic performance of alloy further improves.
Embodiment 3
Employing the invention provides method and prepares the Fe-49Co-2V-0.7Cr magnetically soft alloy material, and the concrete technology step is as follows:
Purity be 99.99% Fe and purity be 99.9% Co, V, Cr according to atomic percent Fe-49Co-2V-0.7Cr proportioning, carry out arc melting through argon shield.Then, after 1200 ℃, vacuum is carried out 4h diffusion annealing, the alloy furnace cooling.Afterwards, melted ingot is forged, forging temperature is 1150 ℃, the thickness 10mm after forging.Be hot-rolled down to 3mm afterwards after 1000 ℃ of lower alloy insulations 1.Carry out afterwards deflection and be 30% cold rolling processing.Cold rolling sheet material is carried out the final thermal treatment of vacuum of 2h differing temps, final thermal treatment temp is respectively 550 ℃, 600 ℃, 670 ℃, 760 ℃, 800 ℃ and 850 ℃, 10 ℃/min of temperature rise rate, and the type of cooling is air cooling.
Fig. 1 (d) is the tissue topography after embodiment 3 interalloy high-temperature heat treatment (760 ℃～850 ℃).As seen from the figure, adding of 0.7%Cr produced a large amount of precipitated phases, forces crystal grain generation dispersion.After 760 ℃ of processing, the dispersion of crystal grain is inhomogeneous, still has the larger crystal grain of part, after 800 ℃ of processing, and the zone that dispersion is inhomogeneous, grain-size diminishes, and to 850 ℃ of thermal treatments, the crystal grain dispersion is very even, and grain-size is in 10 μ m.Along with the rising of thermal treatment temp, precipitated phase content also increases to some extent.Due to the acting in conjunction of precipitation strength and refined crystalline strengthening, the tensile strength of Fe-49Co-2V-0.7Cr alloy is higher, and grain refining also makes alloy plasticity improve simultaneously.
Fig. 3 is the fracture apperance figure of embodiment 3 interalloy test blocks, adopts scanning electronic microscope (CamScan3400) to take.Cold rolling attitude alloy (as-rolled) fracture is typical dimple pattern, and alloy toughness is better, and unit elongation is higher.The order-disorder transition temperature of FeCo alloy is 730 ℃, and the membership that adds of V decreases this transition temperature.Carry out final thermal treatment in lower than the order-disorder transition temperature range, namely alloy is in ordered region thermal treatment, and alloy ordering degree is relatively high, and fracture is typical fragility cleavage fracture, and river pattern is high-visible, therefore alloy is more crisp, unit elongation is lower; Carry out final thermal treatment in higher than the order-disorder transition temperature range, because the type of cooling is air cooling, alloy still can produce the certain ordered phase, but the ordering degree decreases, and fracture is typical quasi-cleavage fracture, as shown in dotted portion in figure, existence is by the cleavage lines of dimple expansion, although there is certain river pattern, area reduces and length shortens, therefore alloy plasticity improves, unit elongation improves.
Embodiment 4
Adopt preparation method provided by the invention, also prepared the alloy of Cr content 0.3～1.0 in the present embodiment, all the other preparation technology's flow processs are with embodiment 2.
Fig. 4 is the coercive force curve of Fe-49Co-2V-xCr alloy after cold rolling attitude and heat treatments at different, adopts DC B-H magnetic hysteresis loop tester (DC B-H loop tracer) test.After cold rolling without the sample of Overheating Treatment because cold rolling rear unrelieved stress is very large, cause the high-coercive force of alloy.By thermal treatment, coercive force can decrease; Along with thermal treatment temp raises, sample generation recovery and recrystallization, crystallization degree raises, because crystal boundary moves the formation resistance to domain wall, therefore coercive force can raise to some extent; And along with temperature further improves, grain growth, crystal boundary density reduces, and coercive force reduces thereupon; After higher than 800 ℃, the precipitated phase showed increased of rich V and Cr is distributed in around crystal grain, forms the domain wall moving resistance, and coercive force rises to some extent.Along with the increase of Cr content, the coercive force curve moves on the whole, i.e. alloy coercive force after uniform temp thermal treatment raises.
Fig. 5 and Fig. 6 are tensile strength and the unit elongation result curve of Fe-49Co-2V-xCr alloy after cold rolling attitude and heat treatments at different, the data tension test tester (INSTRON5565-50kN) test.There is drawing hardening effect in sample without Overheating Treatment after cold rolling, and alloy strength is higher.Along with thermal treatment temp raises, the defectives such as dislocation reduce, lattice distortion weakens, drawing hardening effect reduces, alloy strength reduces, and belongs to ordered region thermal treatment lower than 700 ℃ of lower thermal treatments simultaneously, and alloy ordering degree is high (and thinks that thermal treatment temp is higher, the ordering degree is higher), alloy fragility is obvious.And higher than 700 ℃ of thermal treatments, enter region of disorder thermal treatment, and ordering degree relative reduce, plasticity increases.Simultaneously, after 760 ℃, thermal treatment temp raises, and grain refining and precipitation strength are obvious, and intensity improves.
Matrix alloy of the present invention is the Fe-49Co-2V alloy, adopts method provided by the invention to be prepared from.After Overheating Treatment, soft magnetic performance is excellent, and coercive force can reach 0.45～2Oe.But structurally, carry out final thermal treatment in 760～850 ℃ of scopes after, as shown in Fig. 1 (a), without obviously separating out, along with thermal treatment temp raises, grain-size is grown up, and mechanical property can descend along with the reduction of grain-size, in the time of 800 ℃, tensile strength only has 495MPa, discontented full border application demand.Specific performance sees Table 3.
Table 3Fe-49Co-2V matrix alloy performance table
Claims (7)
1. FeCoVCr non-retentive alloy, it is characterized in that: described FeCoVCr non-retentive alloy is Fe-49Co-2V-xCr, wherein 0＜x≤1.0, more than be atomic percent.
2. FeCoVCr non-retentive alloy, it is characterized in that: described FeCoVCr non-retentive alloy is the Fe-49Co-2V-xCr alloy, wherein 0＜x＜0.5, more than be atomic percent.
3. alloy according to claim 1, it is characterized in that: described FeCoVCr non-retentive alloy is the Fe-49Co-2V-0.3Cr alloy, and after 850 ℃ of final thermal treatments of described non-retentive alloy, obtaining performance is coercive force 3.58Oe, tensile strength 868MPa, unit elongation 8.3%.
4. alloy according to claim 1 is characterized in that: in described non-retentive alloy microstructure, separates out at the grain boundaries particle that is magnetic, and precipitated phase particle size 0.3～1.2 μ m, percent by volume is 5～16%.
5. the preparation method of a non-retentive alloy claimed in claim 1, is characterized in that comprising the steps:
The first step is carried out the proportioning melting with raw material, and the melting mode is vacuum arc furnace melting;
Second step, vacuum diffusion annealing, temperature 〉=900 ℃, annealing time 2～10h, melted ingot furnace cooling;
The 3rd step, high temperature forging; Forging temperature is higher than 800 ℃;
The 4th step is to forging bulk through the hot rolling of the continuous three above passages of passage;
In the 5th step, alloy carries out cold rolling processing sheet material, sheet material, deflection 10～95%;
In the 6th step, alloy carries out final thermal treatment, and temperature is divided into 350～980 ℃, and heat treatment time is 2h, and the type of cooling is air cooling.
6. the preparation method of non-retentive alloy according to claim 5, is characterized in that comprising the steps:
The first step is carried out the proportioning melting with raw material, and the melting mode is vacuum arc furnace melting;
Second step, vacuum diffusion annealing, temperature 〉=1200 ℃, annealing time 4～10h, melted ingot furnace cooling;
The 3rd step, high temperature forging; Forging temperature is higher than 1100 ℃;
The 4th step is to forging bulk through the hot rolling of the above passage of continuous four-pass.
In the 5th step, alloy carries out intermediate heat treatment, and condition is 750～970 ℃, 〉=10min;
In the 6th step, alloy carries out cold rolling processing sheet material, sheet material, deflection 〉=30%;
In the 7th step, alloy carries out final thermal treatment, and temperature is divided into 550～850 ℃, and heat treatment time is 2h, and the type of cooling is air cooling.
7. the preparation method of according to claim 5 or 6 described non-retentive alloys is characterized in that: in the 6th step, final thermal treatment temp is 760～850 ℃.
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| CN110438308A (en) * | 2019-09-16 | 2019-11-12 | 哈尔滨工业大学 | A kind of multistage heat treatment method of FeCo-1.1V magnetically soft alloy |
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| CN114645173A (en) * | 2020-12-18 | 2022-06-21 | 孙学银 | High-strength FeCoV-Nb-W soft magnetic alloy and heat treatment method thereof |
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| US3597286A (en) * | 1968-02-23 | 1971-08-03 | Westinghouse Electric Corp | Method of treating a high strength high ductility iron-cobalt alloy |
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| CN104480351A (en) * | 2015-01-06 | 2015-04-01 | 上海康晟特种合金有限公司 | Ferrum-cobalt-vanadium super alloy and preparation method thereof |
| CN111373494A (en) * | 2017-10-27 | 2020-07-03 | 真空融化股份有限公司 | High permeability soft magnetic alloy and method for manufacturing high permeability soft magnetic alloy |
| CN111373494B (en) * | 2017-10-27 | 2022-02-18 | 真空融化股份有限公司 | High permeability soft magnetic alloy and method for manufacturing high permeability soft magnetic alloy |
| CN110129535A (en) * | 2019-06-17 | 2019-08-16 | 陕西新精特钢研精密合金有限公司 | A kind of high intensity 1J22 bar and preparation method thereof |
| CN110438308A (en) * | 2019-09-16 | 2019-11-12 | 哈尔滨工业大学 | A kind of multistage heat treatment method of FeCo-1.1V magnetically soft alloy |
| CN112430720A (en) * | 2020-11-13 | 2021-03-02 | 沈阳航天新光集团有限公司 | Soft magnetic alloy annealing process |
| CN114645173A (en) * | 2020-12-18 | 2022-06-21 | 孙学银 | High-strength FeCoV-Nb-W soft magnetic alloy and heat treatment method thereof |
| CN113913649A (en) * | 2021-10-14 | 2022-01-11 | 陕西新精特钢研精密合金有限公司 | 1J22 alloy with high mechanical property and high magnetic property and manufacturing process thereof |
| CN113913649B (en) * | 2021-10-14 | 2022-08-02 | 陕西新精特钢研精密合金有限公司 | 1J22 alloy with high mechanical property and high magnetic property and manufacturing process thereof |
| CN114318172A (en) * | 2022-01-04 | 2022-04-12 | 西南科技大学 | Iron-nickel alloy with ultrahigh soft magnetic performance and preparation method thereof |
| CN114318172B (en) * | 2022-01-04 | 2022-11-18 | 西南科技大学 | Iron-nickel alloy with ultrahigh soft magnetic performance and preparation method thereof |
| CN114703413A (en) * | 2022-03-28 | 2022-07-05 | 常州大学 | Multiphase multi-principal-element alloy with controllable phase content and preparation method thereof |
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