CN103691741A - Manufacturing method of making fe-a1 alloy strip steel - Google Patents
Manufacturing method of making fe-a1 alloy strip steel Download PDFInfo
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- CN103691741A CN103691741A CN201310452556.XA CN201310452556A CN103691741A CN 103691741 A CN103691741 A CN 103691741A CN 201310452556 A CN201310452556 A CN 201310452556A CN 103691741 A CN103691741 A CN 103691741A
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Abstract
The invention provides a manufacturing method of making Fe-A1 alloy strip steel without cracks in the process of cold rolling. The Fe-A1 alloy strip steel is made up of A1: 4.0% to 10.0%, margin Fe and impurities. The method includes: (1) under the temperature of 800 to 1100 DEG C, conducting hot rolling on the hot rolling perform body and make the hot rolling material at 3.00mm thickness; (2) conducting cold rolling at calendar rate 30% and making the cold rolling material at 1.4mm thickness.
Description
Technical field
The present invention relates to Fe-Al is the manufacture method of alloy band steel.
Background technology
Along with the noise such as automobile etc. and the problem of vibration are seriously changed, there is the demand of the metal material (noiseless alloy) of vibration damping excellence.As aforesaid noiseless alloy, known such as Fe-Al alloy, Fe-Cr-Al alloy, Fe-Co-V alloy, Mn-Cu alloy, Mg alloy etc., for various uses.Wherein Fe-Al alloy is known as cost of material cheapness, has the noiseless alloy of excellent vibration damping.
Manufacture method as this Fe-Al alloy sheets, for example TOHKEMY 2005-29889 communique (patent documentation 1) discloses following operation: will contain C:0.001～0.01% in quality %, Si :≤3.0%, Mn:0.01～3.0%, P :≤0.02%, S :≤0.01%, Al:5.0～10.0%, N:0.001～0.05%, the Fe of surplus and the inevitably plate slab of impurity are heated to 1100 ℃ of above temperature, at least comprise the more than 1 passage hot rolling of more than 30% heavy reduction rate of rate under more than 1000 ℃ temperatures, and under more than 800 ℃ final rolling temperatures, carry out hot rolling.
prior art document
patent documentation
Patent documentation 1: TOHKEMY 2005-29889 communique
Summary of the invention
the problem that invention will solve
Above-mentioned Fe-Al alloy, owing to containing a large amount of Al, is therefore considered to the alloy of poor in processability.For example, in aforesaid patent documentation 1, also for thickness, not disclose, is even also indefinite for whether being suitable for obtaining the thin cold rolling material of 1.5mm about following.In fact, present situation is not have to take the form of coiled material shape to produce the thin technology with steel of thickness below 1.5mm.In fact, when wanting to carry out the cold rolling Fe-Al of manufacture with the hot rolling material of disclosed composition in patent documentation 1 while being alloy band steel, when cold rolling, crackle takes place frequently.
Hot rolling material is carried out when cold rolling, carried out cold rolling cold rolling material and sometimes having bent.The cold rolling material of this bending is carried out when cold rolling again, and bending stress is carried on steel plate, and its result is likely cracked by the maximum position of load from stress.It in the ferritic steel with a large amount of Al of containing of ductile brittle transition temperature, is particularly serious problem.
The object of the present invention is to provide the Fe-Al that suppresses crackle in cold rolling process is the manufacture method of alloy band steel.
for the scheme of dealing with problems
The inventor prevents during the Fe-Al in poor in processability is associated to gold that the method for the generation of the crackle in cold rolling process from having carried out various research, found that by being controlled in hot rolling below specific thickness, can prevent the generation of the crackle in cold rolling, thereby reach the present invention.
That is, the present invention relates to Fe-Al is the manufacture method of alloy band steel,
Described Fe-Al is that alloy band steel is formed by Fe and the impurity of Al:4.0～10.0%, surplus in quality %, and described manufacture method comprises:
(1) at 800～1100 ℃, to thering is the hot rolling of aforementioned component, with blank, carry out hot rolling, make the hot-rolled process that thickness is the hot rolling material below 3.0mm, and
(2) to aforementioned hot stocking carry out calendering rate more than 30% cold rolling, make the cold rolling process that thickness is the cold rolling material below 1.4mm.
In addition after the preferred aforementioned cold rolling process of the present invention,
Carry out (3) the cold rolling material being obtained by aforementioned cold rolling process is batched to the coiling process into coiled material.
The calendering rate of preferred aforesaid hot rolling in the present invention is more than 90%.
the effect of invention
According to the present invention, can be manufactured on the Fe-Al that suppresses crackle in cold rolling process is alloy band steel.
Accompanying drawing explanation
Fig. 1 is the schematic diagram of repeated flex test method.
Fig. 2 is the test film outward appearance photo after cold rolling.
description of reference numerals
1. rectangular strip test film
2. stationary fixture
The specific embodiment
The invention is characterized in, be the hot rolling Fe-Al material below 3.0mm by manufacturing thickness, and can be manufactured on the Fe-Al that suppresses crackle in cold rolling process is alloy band steel.Below, technical characterictic of the present invention is described.
First, the inventor waits the thickness of Fe-Al alloy and the relation of processability evaluated.Evaluation is that to use the Fe-Al implemented hot rolling be alloy band steel, prepares the different Fe-Al of thickness of slab be associated gold ribbon steel sample by plane lapping, implements repeated flex and tests.Conventionally by the cold rolling thickness that changes, but this to use parallel grinding be in order to get rid of the impact of the processing strain producing when cold rolling on thickness adjustment.
The evaluation of specifically carrying out is as described below.
By vacuum melting, carry out the 10kg steel ingot being formed by Al approximately 8%, surplus Fe and impurity shown in melting table 1.Then, aforementioned Fe-Al is associated to the forge hot producing material that golden Heating Steel Ingots to 1100 ℃ carries out warm and hot forging, makes thickness 35mm.
Then, aforementioned hot is forged to the hot rolling that material is again heated to 1100 ℃, applies 91% calendering rate, make the hot rolling material of thickness 3.2mm.Then, aforementioned hot stocking is cut into the rectangular strip test film of width 8mm, length 80mm.Then, rectangular strip test film is implemented to plane lapping, every kind of thickness of rectangular strip test film that thickness is different is prepared to 2 pieces.It should be noted that, the thickness of the rectangular strip test film of preparation is the 3.2mm before 1.0mm, 1.5mm, 1.75mm, 2.0mm, 2.5mm and plane lapping.
Use these rectangular strip test films, instead cold rolling evaluation, carries out repeated flex test at normal temperatures.The schematic diagram of repeated flex test method shown in Figure 1.As shown in Figure 1, with stationary fixture 2 clamping rectangular strip test films 1, rectangular strip test film 1 being carried out to 90 ° of bendings along direction shown in arrow, is that 1 time, reciprocal 90 ° of bendings are 2 times toward retrying toward retrying by 90 ° crooked 1.Repeat afterwards this test, instrumentation is until the number of times of fracture.Table 2 is illustrated in the result of in each thickness of slab, each thickness respectively being carried out 2 repeated flex tests, its average repeated flex number of times.
[table 1]
[table 2]
As shown in Table 2 above, known along with the attenuation of rectangular strip test film thickness of slab, number of bends increases.In other words, the known thickness of slab attenuation along with hot rolling material, cold-workability rises.Therefore,, by making hot rolling material attenuation, can reduce the risk that the crackle in cold rolling produces.In addition, thickness of slab is that the number of bends of sample of 2.5mm and the number of bends of the sample of 3.2mm are in a ratio of its 2 times, if use thickness of slab is the hot rolling material below 3.0mm, at left and right directions, at least do not produce fracture during each cyclic bending of 1 time, be therefore judged as can be cold rolling level.
Therefore, by aforesaid hot rolling material, take the cold rolling test film of using, by plane lapping, thickness of slab is adjusted to 1.75mm, cold rolling cold rolling with test film enforcement to this with the calendering rate of 1 passage 37%, 46%.In Fig. 2, represent the test film outward appearance photo after cold rolling.
As can be seen from Figure 2, even if apply the cold rolling of heavy reduction rate, can in cold rolling material, not crack yet.Thus, known thickness of slab is 3.0mm when following, even surpass under 30% large calendering rate in the 1st passage when cold rolling, the cold rolling crackle with test film can not produce yet.Can under large calendering rate, implement cold rollingly to occupy advantage in having confirmed productivity.
For implementing in the present invention hot rolling, thickness is adjusted into the reason below 3.0mm above.Be preferably below 2.5mm, more preferably below 2.0mm.
Then the restriction reason that, narration forms.
Al：4.0～10.0%
By the Fe-Al stipulating in the present invention, be alloy band steel while being used as noiseless alloy, thereby Al contribute to vibration damping for solid solution makes magnetostriction increase in Fe and must add.During Al less than 4.0%, vibration damping can not be given full play to.On the other hand, when Al surpasses 10.0%, Fe3Al separates out, damages processability.By above situation, Al is made as 4.0～10%.Under preferred Al, be limited to 7.0%, on preferred Al, be limited to 9.0%.
Surplus Fe and impurity
In the present invention, except aforesaid Al, be Fe and impurity.In aforesaid impurity, as representational impurity, can list C, Si, Mn, P, S, Cr, Ni, Cu, N and O.These impurity elements can be made as: C≤0.1%, Si≤0.3%, Mn≤0.35%, P≤0.015%, S≤0.005%, Cr≤0.15%, Ni≤0.2%, Cu≤0.08%, N≤100ppm and O≤100ppm.If aforesaid content, not hindering Fe-Al is the manufacturing of alloy band steel.
Then, the restriction reason in the manufacture method of narration except the thickness of aforesaid hot rolling material.
Hot-rolled temperature: 800～1100 ℃
In the present invention, the temperature of hot rolling is made as to 800～1100 ℃.This is owing to can obtain high hot-workability in this temperature range.During 800 ℃ of hot-rolled temperature less thaies, large, the percentage elongation of the hot strength of Fe-Al alloy significantly reduces.Therefore,, when 800 ℃ of less thaies are carried out hot rolling, the crackle of Fe-Al alloy band steel produces.In addition, the upper limit of hot-rolled temperature is made as to 1100 ℃, the percentage elongation that is Fe-Al alloy while surpassing 1100 ℃ because of hot-rolled temperature has saturated tendency, even if carry out hot rolling in surpassing the temperature province of 1100 ℃, is also being difficult to obtain the effect that hot-workability further rises.And the oxide layer that hot-rolled temperature is higher, form on the top layer of Fe-Al alloy is thicker, therefore for remove supply with to after hot rolling, carry out cold rolling in hot rolling material surface on formed oxide layer and expend a large amount of man-hours, be uneconomic.
Due to above reason, the temperature range of hot rolling is made as to 800～1100 ℃.Preferably hot-rolled temperature under be limited to 900 ℃, preferably hot-rolled temperature on be limited to 1050 ℃.
The calendering rate of hot rolling: more than 90%
Calendering rate during in the present invention, preferably by hot rolling is made as more than 90%.This is because, the calendering rate of hot rolling is 90% when above, is carried on dependent variable homogenising in hot rolling material of hot rolling material, below during operation cold rolling, can suppress more reliably crackle and produce.For the upper limit, the calendering rate that hot rolling material can be made below 2.0mm of take is the upper limit, if consider the ability of hot-rolling mill, in the calendering rate of hot rolling, is limited to 98% left and right.
In the present invention, be that the temperature range of aforesaid hot rolling is implemented hot rolling, made after the hot-rolled process that thickness is the hot rolling material below 3.0mm, move on to cold rolling process.It should be noted that, certainly can between hot-rolled process and cold rolling process, also comprise the operation of removing the oxide layer being formed by hot rolling.
For the cold rolling process of stipulating in the present invention, describe below.
Calendering rate: more than 30%
The object of the cold rolling thickness with the regulation made and by the cold rolling object that applies strain.By cold rolling, apply processing strain, while then annealing, can make crystalline particle miniaturization and make Fe-Al is that the intensity of alloy band steel rises.During calendering rate less than 30%, it is not enough that crystalline particle micronized effect becomes, and its result can not obtain enough intensity.Therefore, the calendering rate to aforementioned hot stocking is made as more than 30%.Therefore it should be noted that, for the upper limit, also have relation with the thickness of hot rolling material and the cold rolling material of specific thickness, cannot treat different things as the same, if but situation of the present invention next be 99.9% left and right.
Thickness: below 1.4mm
In the present invention, take aforementioned more than 30% calendering rate makes the cold rolling material of thickness below 1.4mm.It is to be that the rigidity of alloy band steel reduces, local stress while making to batch into coiled material reduces in order to make Fe-Al below that thickness is made as to 1.4mm.And about lower limit, be not particularly limited, but during the not enough 0.03mm of the thickness of cold rolling material, worry the THICKNESS CONTROL difficulty that becomes, to be therefore made as 0.03mm be preferred to the lower limit of the thickness of cold rolling material.
Coiled material coiling process
In the present invention, as described above, can prevent the generation of crackle when cold rolling, therefore the cold rolling material of cold rolling mistake can be batched as coiled material.During application coiled material coiling process, compare with the operation of the cold rolling material being obtained by cold rolling process being made to sheet steel plate, can make productivity increase tremendously.
embodiment
(embodiment 1)
By vacuum melting, come the Fe-Al shown in melting table 3 to be associated the steel ingot of golden 2600kg.Then, by these Heating Steel Ingots to 1000 ℃, carry out warm and hot forging, obtain the forge hot producing material of thickness 55mm.Then, in order to remove surface blemish, with grinder, the surface of this forge hot producing material is ground, obtain the forge hot producing material of thickness 53mm.
[table 3]
The forge hot producing material of manufacturing for the 2600kg steel ingot by No.1 carries out hot rolling at 1000 ℃.Calendering rate is made as to 97%, obtain thickness 1.7mm hot rolling material, coil into coiled material.
This coils of hot rolled is carried out after pickling removes surperficial oxide layer, implementing cold rolling.Respectively the cold rolling material of the cold rolling material of the thickness 0.8mm obtaining for 53% time in calendering rate and the thickness 0.5mm that obtains for 71% time in calendering rate is batched and becomes coiled material.During this cold rolling process, at Fe-Al, be in alloy band steel, also not find the generation of crackle.
In addition, the forge hot producing material of manufacturing for the 2600kg steel ingot by No.2 carries out hot rolling at 1000 ℃.Calendering rate is made as to 95%, obtain thickness 2.6mm hot rolling material, coil into coiled material.
This coils of hot rolled is carried out after pickling removes surperficial oxide layer, implementing cold rolling.Obtain calendering rate and be 69%, the cold rolling material of the cold rolling material of thickness 0.8mm and the thickness 0.5mm of calendering rate 81%, resulting Fe-Al is associated to golden strip coiling becomes coiled material.During this cold rolling process, at Fe-Al, be associated the generation that Jin Zhongye does not find crackle.
(embodiment 2)
By vacuum melting, come the Fe-Al shown in melting table 4 to be associated the steel ingot of golden 400kg.Then, by these Heating Steel Ingots to 1000 ℃, carry out warm and hot forging, then, in order to remove surface blemish, with grinder, the surface of this forge hot producing material is ground, is obtained the forge hot producing material of thickness 55mm.The composition of steel ingot shown in table 4.
[table 4]
The forge hot producing material of manufacturing for the 400kg steel ingot by No.3 and No.4 carries out hot rolling at 1000 ℃.Calendering rate is made as to 95%, obtain thickness 2.6mm hot rolling material, coil into coiled material.
This coils of hot rolled is carried out after pickling removes surperficial oxide layer, implementing cold rolling.Obtain calendering rate and be 69%, the cold rolling material of the cold rolling material of thickness 0.8mm and the thickness 0.5mm of calendering rate 81%, resulting Fe-Al is associated to golden strip coiling becomes coiled material.During this cold rolling process, at Fe-Al, be associated the generation that Jin Zhongye does not find crackle.
From above results verification to: by making thickness of slab, be the hot rolling material below 3.0mm, it is possible can preventing defects i.e.cracks, at the coiled material that has no the cold rolling material of enforcement in the past, batch.
utilizability in industry
Fe-Al according to the present invention is the manufacture method of alloy band steel, can be that Fe-Al below 1.4mm is associated gold ribbon steel and makes coiled material shape by thickness, therefore to requiring the application of the purposes of thinness and wide cut material to become possibility.
Claims (3)
1. Fe-Al is a manufacture method for alloy band steel, it is characterized in that, described Fe-Al is that alloy band steel is formed by Fe and the impurity of Al:4.0～10.0%, surplus in quality %, and described manufacture method comprises:
(1) at 800～1100 ℃, to thering is the hot rolling of described composition, with blank, carry out hot rolling, make the hot-rolled process that thickness is the hot rolling material below 3.0mm, and
(2) to described hot rolling material carry out calendering rate more than 30% cold rolling, make the cold rolling process that thickness is the cold rolling material below 1.4mm.
2. Fe-Al according to claim 1 is the manufacture method of alloy band steel, it is characterized in that, after described cold rolling process,
Carry out (3) the cold rolling material being obtained by described cold rolling process is batched to the coiling process into coiled material.
3. Fe-Al according to claim 1 and 2 is the manufacture method of alloy band steel, it is characterized in that, the calendering rate of described hot rolling is more than 90%.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2012-214946 | 2012-09-27 | ||
| JP2012214946 | 2012-09-27 | ||
| JP2013-177708 | 2013-08-29 | ||
| JP2013177708A JP2014080676A (en) | 2012-09-27 | 2013-08-29 | PRODUCTION METHOD OF Fe-Al BASED ALLOY BAND-STEEL |
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| CN103691741A true CN103691741A (en) | 2014-04-02 |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113637920A (en) * | 2021-08-19 | 2021-11-12 | 西南交通大学 | Multi-element Fe-Al-based damping alloy and preparation method thereof |
| CN113874140A (en) * | 2019-05-31 | 2021-12-31 | 日立金属株式会社 | Fe-Al alloy vibration damping member and method for manufacturing same |
| CN116507745A (en) * | 2021-09-14 | 2023-07-28 | 株式会社博迈立铖 | Fe-Co alloy bar |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113874140A (en) * | 2019-05-31 | 2021-12-31 | 日立金属株式会社 | Fe-Al alloy vibration damping member and method for manufacturing same |
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Application publication date: 20140402 |