CN104169027A - Fe-Al ALLOY PRODUCTION METHOD - Google Patents
Fe-Al ALLOY PRODUCTION METHOD Download PDFInfo
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- CN104169027A CN104169027A CN201380012914.3A CN201380012914A CN104169027A CN 104169027 A CN104169027 A CN 104169027A CN 201380012914 A CN201380012914 A CN 201380012914A CN 104169027 A CN104169027 A CN 104169027A
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- ingot
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- oxide film
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 29
- 229910000838 Al alloy Inorganic materials 0.000 title abstract description 5
- 239000000463 material Substances 0.000 claims abstract description 51
- 238000005097 cold rolling Methods 0.000 claims abstract description 32
- 238000005098 hot rolling Methods 0.000 claims abstract description 19
- 239000012535 impurity Substances 0.000 claims abstract description 16
- 238000005242 forging Methods 0.000 claims abstract description 14
- 238000000137 annealing Methods 0.000 claims abstract description 9
- 238000005266 casting Methods 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 33
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims description 22
- 229910052737 gold Inorganic materials 0.000 claims description 22
- 239000010931 gold Substances 0.000 claims description 22
- 230000001590 oxidative effect Effects 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 abstract description 5
- 238000000605 extraction Methods 0.000 abstract description 2
- 239000013078 crystal Substances 0.000 description 16
- 208000037656 Respiratory Sounds Diseases 0.000 description 14
- 238000013016 damping Methods 0.000 description 14
- 238000009863 impact test Methods 0.000 description 12
- 229910045601 alloy Inorganic materials 0.000 description 11
- 239000000956 alloy Substances 0.000 description 11
- 239000007789 gas Substances 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 238000005336 cracking Methods 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 230000019771 cognition Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000006378 damage Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 239000000284 extract Substances 0.000 description 2
- 230000001788 irregular Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910020516 Co—V Inorganic materials 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910002060 Fe-Cr-Al alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
- 230000001360 synchronised effect Effects 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000012795 verification Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/04—Shaping in the rough solely by forging or pressing
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D30/00—Cooling castings, not restricted to casting processes covered by a single main group
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Forging (AREA)
- Metal Rolling (AREA)
Abstract
Provided is a Fe-Al alloy production method capable of effectively preventing cracks from occurring during production. This Fe-Al alloy production method involves an ingot production step for casting an Fe-Al alloy which contains 2.0-9.0 mass% Al and the rest of which consists of Fe and impurities to obtain ingots by extraction from the mold, a hot forging step for hot forging the ingots to obtain a hot forged material, a hot rolling step for hot rolling the hot forged material to obtain a hot-rolled material, an oxide film removal step for removing the oxide film from the hot-rolled material to obtain a material for cold rolling, a cold rolling step for cold rolling the material for cold rolling to obtain a cold-rolled material, and an annealing step for annealing the cold-rolled material, wherein heating of the ingots in the hot forging step is started before the surface temperature of the ingots extracted from the mold in the ingot production step is cooled to less than 250 DEG C.
Description
Technical field
The present invention relates to Fe-Al and be associated golden manufacture method.
Background technology
Along with the noise of such as automobile etc. and the aggravation of the problem of vibration, the demand growth of the metal (hereinafter referred to as damping alloy) of damping and amortization excellence.As damping alloy, known Fe-Cr-Al alloy, Fe-Co-V alloy, Mn-Cu alloy, Mg alloy etc., be used in various uses.
Wherein, cheap and have the metal of excellent damping and amortization as cost of material, also known Fe-Al is associated gold, knownly contains Al taking quality % and is associated also excellent (patent documentation 1) of golden soft magnetic characteristic as 2～12% Fe-Al.
Fe-Al as above-mentioned damping and amortization excellence is associated golden manufacture method, discloses a kind of manufacture method, and it comprises following operation: be 2～12 quality % for Al content, and the operation that the alloy that surplus is made up of Fe and inevitable impurity carries out plastic working; Carry out the operation of cold rolling processing for the alloy through plastic working; And under more than 5% condition, carry out by sectional shrinkage being the operation (patent documentation 1) that the alloy after cold rolling processing is annealed under the temperature conditions of 400～1200 DEG C.
Prior art document
Patent documentation
Patent documentation 1: public table patent WO2006/085609 communique again
Invent problem to be solved
Be associated gold as the Fe-Al that can expect as described so serviceability, according to the inventor's research, it is extremely low that Fe-Al is associated gold toughness at normal temperatures, in the time that ingot size is large, for example, when 100kg is above, likely because ingot is inner and surperficial cooling velocity is different and the processing such as de-ingot operates crackle occurs.In addition, because Fe-Al is associated the Al that gold contains easy oxidation in a large number, so the crust of ingot is easily coarse, worry also to occur because toughness is low crackle.
Summary of the invention
The object of the invention is to, provide a kind of Fe-Al that crackle occurs can effectively prevent from manufacturing time to be associated golden manufacture method.
For solving the means of problem
The inventor draws following cognition: the Fe-Al of casting is associated golden ingot and presents and organize thick columnar structure, and in addition, the crackle risk causing due to the proterties of ingot is high, on the other hand, if first via hot forging process, can reduce the risk of crackle.And, that studies based on this cognition found that, Fe-Al is associated gold can improve significantly toughness more than specified temp, makes ingot not be cooled to enter into hot forging process under the state lower than set point of temperature, can reduce the risk of crackle, thereby reach the present invention.
That is, the present invention is that a kind of Fe-Al is associated golden manufacture method, and it possesses following operation:
Ingot manufacturing process, casting contains Al:2.0～9.0% in quality %, and the Fe-Al that surplus is made up of Fe and impurity is associated gold, takes out and obtain ingot from mold;
Hot forging process, ingot described in forge hot and become forge hot material;
Hot-rolled process, forge hot material described in hot rolling and become hot rolling material;
Oxide film thereon is removed operation, removes the oxide film thereon of described hot rolling material and becomes the cold rolling former material of using;
Cold rolling process, the former material of cold rolling described cold rolling use and become cold rolling material; And
Annealing operation, anneals for described cold rolling material,
Wherein, in described ingot manufacturing process, before the surperficial surface temperature of the described ingot taking out is cooled to lower than 250 DEG C, start the heating of the described ingot of described hot forging process from mold.
In addition, in the present invention, be associated gold for described Fe-Al and be associated gold, can also contain in quality % the Nb below 1.0%.
In addition, in the present invention, preferably before the surface temperature of the described ingot obtaining via described ingot manufacturing process is cooled to lower than 250 DEG C, and after the ingot surface of the oxide film thereon through removing described ingot surface is removed operation, enter into described hot forging process.
In addition, preferably applicable annealing operation is carried out in non-oxidizing gas atmosphere in the present invention.
Invention effect
According to the present invention, can effectively prevent from being associated at Fe-Al the crackle occurring when gold is manufactured.
Brief description of the drawings
Fig. 1 represents that Fe-Al is associated the figure of golden pendulum impact test example.
Fig. 2 represents that Fe-Al is associated the figure of golden pendulum impact test example.
Detailed description of the invention
Important feature of the present invention is, so that the ingot after casting is not cooled to keep temperature and enter into hot forging process lower than the mode of set point of temperature.Below, be at length illustrated.
Being associated gold as the Fe-Al that contains 2.0～9.0% Al in quality % of object of the present invention is the alloy of having given play to excellent damping and amortization.Confirm on the other hand: the Fe-Al of casting is associated golden ingot, form thick columnar structure, because the adhesion of crystal grain boundary is little, so easily there is intercrystalline cracking.But also confirm: because Fe-Al is associated, gold intensity is at normal temperatures low and toughness is extremely low, so even crackle also easily occurs in the impact of a little.
The inventor is associated golden toughness for such Fe-Al and is studied.Specifically, be to extract from the ingot of casting the test film that pendulum impact test is used, carry out pendulum impact test.It should be noted that, the Al that the composition of the ingot of extraction pendulum impact test sheet contains 8 quality %, surplus is Fe and impurity.
The result of the pendulum impact test of above-mentioned test film shown in Fig. 1.As shown in Figure 1, the toughness that confirms pendulum impact test sheet at 225 DEG C is increased sharply, can be to 300J/cm in the temperature field more than 250 DEG C
2hI high impact value.In addition, observed by the plane of disruption of pendulum impact test sheet and the results verification of impact test to: when lower than 250 DEG C, brittle fracture becomes restriction.
According to these result of the tests, the inventor finds: even the adhesion of crystal grain boundary is little, easily occur under the state of ingot of intercrystalline cracking, if make ingot not be cooled to lower than the temperature field of 250 DEG C and enter into forge hot, the occurrence risk of crackle can reduce.Further, as making ingot not be cooled to the method lower than set point of temperature, the easiest is to take off ingot at manageable high-temperature-range, shortens the transit time to forge hot.Certainly, also can protect mild heat for ingot in during transition.
Further, why specifying the surface temperature of the ingot taking out from mold in the present invention, is because the surface of ingot is the most cooling.The surface temperature of ingot can be used the simple thermometers such as such as infrared ray thermal image instrument to measure easily.
In the present invention, as described so, make the surface temperature of the ingot taking out from mold not be cooled to enter into lower than 250 DEG C described hot forging process, reduce the occurrence risk of crackle.Thus, the generation of microscopic checks is suppressed, can prevent that crackle is obviously changed in the time of forge hot.
As the condition of hot forging process, for example, ingot can be heated to the temperature of 1000 DEG C～1200 DEG C, carry out forge hot and become forge hot material with 850 DEG C of above temperature.There is the metal structure of destruction (extension) because of becoming thick crystal grain in forge hot material, so can not make crackle occur after forge hot and be cooled to normal temperature.
Further, in order more positively to suppress the generation of above-mentioned microscopic checks, preferably remove Fe-Al to be associated the oxide film thereon of golden ingot surface.The surface configuration that Fe-Al is associated ingot material be exist larger concavo-convex because oxide film thereon is formed on irregular surface, so there is the situation of the starting point that becomes described microscopic checks.Therefore, preferably remove Fe-Al and be associated the oxide film thereon of golden ingot surface.
While removing the oxide film thereon of ingot surface, also need in the temperature field that is not less than 250 DEG C, implement.This be because, as shown in Figure 1, under the state of ingot, low lower than the toughness in the temperature field of 250 DEG C, exist cracking danger.Further, the oxide-film of ingot is removed the grinder of use under for example hot and is ground.This be because, as mentioned above, the surface configuration that Fe-Al is associated ingot material be exist larger concavo-convex, because oxide film thereon is formed on irregular surface, so can, in removing oxide-film, also remove in the lump the concavo-convex of ingot.
Use above-mentioned forge hot material to carry out hot rolling.As the condition of hot rolling, can be heated to the temperature of 1000～1200 DEG C, carry out hot rolling and become hot rolling material with 800 DEG C of above temperature.
Because hot rolling material is formed with oxide film thereon on surface, so remove oxide film thereon as the former material of cold rolling use.Have an oxide-film if remaining on the band after cold rolling, for example remaining have the local damping and amortization of oxide-film likely deteriorated.
Further, as the method for removing of the oxide film thereon of hot rolling material, there is the method such as method, pickling of physically removing.The thickness of nearly 50～100 μ m left and right of oxide film thereon of hot rolling material, therefore, preferably removes oxide film thereon by such as pickling etc.
Use the former material of removing the cold rolling use that operation obtains by above-mentioned oxide film thereon to carry out cold rolling.Cold rollingly carry out for following object: reach the object of expecting thickness; Apply strain by cold rolling, make crystal grain miniaturization give the object of intensity by the annealing of being undertaken by next procedure.
For example, if to make crystal grain become crystal grain diameter be the fine crystal grain of 50～300 μ m and be associated gold to Fe-Al and give intensity by annealing, the reduction ratio of cold rolling process is more than 50%.
Subsequently, anneal and adjust crystal grain diameter, and being associated gold to Fe-Al and giving necessary damping and amortization.At this moment, easily form hard and thin oxide film thereon because be associated gold surface at Fe-Al, so preferably anneal in non-oxidizing atmosphere.
As non-oxidizing atmosphere, can enumerate reduced atmosphere, gas atmosphere etc., the gases such as hydrogen that preferably selection can be annealed continuously, nitrogen, AX gas, Ar gas.
Above, the problem of the crackle when Fe-Al being obtained by manufacture method given to this invention of explanation is associated gold and can prevents from manufacturing, the Fe-Al that produces expeditiously thin thickness is associated gold.
Further, in the present invention, said Fe-Al is associated gold and refers to the Al except containing 2.0～9.0 quality %, beyond the Fe-Al alloy that surplus is made up of Fe and impurity, also further contains the alloy of the three elements below 1 quality %.
In the present invention, why making Al is 2.0～9.0 quality %, is because use Fe-Al given to this invention while being associated gold ribbon as damping alloy, and Al solid solution and magnetostriction is increased in Fe, contributes to damping and amortization thus.For this effect, if Al lower than 2.0 quality % damping and amortization can not give full play to.On the other hand, when Al exceedes 9.0 quality %, separate out Fe
3al, therefore damages processability.
In addition, as the three elements of optionally adding, the element of selecting the miniaturization of the crystal grain to cast sturcture with Fe formation compound to work.Specifically, can enumerate Nb, Ti, Mo, W etc., wherein particularly preferably add Nb.This is because except Nb is less expensive, itself and Fe easily form compound, make Fe
2nb compound is separated out to the crystal grain boundary of cast sturcture, can suppress the formation of thick crystal grain, contributes to the inhibition of intercrystalline cracking.In addition,, if added below 1 quality %, can not hinder hot and processability cold conditions.
In addition, the surplus beyond above-mentioned element is Fe and impurity.As the representative impurity of above-mentioned impurity, can enumerate C, Si, Mn, P, S, Cr, Ni, N and O.These impurity elements are C≤0.01 quality %, Si≤0.2%, Mn≤0.2 quality %, P≤0.01 quality %, S≤0.005 quality %, Cr≤0.05%, Ni≤0.05 quality %, N≤0.01 quality % and O≤0.01 quality %.
Embodiment
First carry out preliminary experiment.Utilize the ingot of the composition shown in vacuum steel ingot making table 1.Extract from the ingot of casting the test film that pendulum impact test is used, carry out pendulum impact test.Pendulum impact test is that test film is heated, kept at the temperature of regulation, and evaluates hot-workability.Evaluation result is shown in Fig. 2.
[table 1]
(quality %)
| ? | Al | Nb | Surplus |
| No.1 | 5.03 | - | Fe and inevitably impurity |
| No.2 | 5.90 | - | Fe and inevitably impurity |
| No.3 | 8.09 | - | Fe and inevitably impurity |
| No.4 | 9.15 | - | Fe and inevitably impurity |
| No.5 | 8.13 | 0.16 | Fe and inevitably impurity |
| No.6 | 8.17 | 0.95 | Fe and inevitably impurity |
"-" symbol indicates without adding.
As shown in Figure 2, known impact characteristics is according to Al addition, Nb addition and different.In No.1,2,3,5 alloy, in the temperature field more than 250 DEG C, can obtain 300J/cm
2hI high impact value.On the other hand, exceeding in the No.4 (9.15%) of Al given to this invention amount, even if be still 100J/cm in the temperature field of 250 DEG C
2low impact value, a part for fracture mode is brittle fracture.
In addition, Al is measured in identical No.3 and No.5, according to the effect of indium addition Nb, in the temperature field more than 200 DEG C, can obtain 300J/cm
2hI high impact value.On the other hand, although to make Nb be 200J/cm up to 0.95% No.6 alloy in the temperature field of 250 DEG C
2low impact value, but because fracture mode is ductility fracture, so think the practical level that reaches.
Taking above-mentioned result as basis, manufacture large-scale steel ingot.Utilize vacuum melting to carry out melting Fe-Al to be associated the ingot of golden 2600kg.Chemical composition is shown in Table 2.
[table 2]
(quality %)
The surface temperature of described ingot of taking out from mold becomes lower than before 250 DEG C, and keeping in holding furnace, heats and manage so that surface of steel ingot temperature is 250 DEG C of above modes.Further, the surface temperature radiation thermometer of putting into the ingot before thermal protection stove is determined as 500 DEG C of left and right.
, ingot from thermal protection stove taken out, be heated to 1000 DEG C with another heating furnace and carry out forge hot, can obtain the forge hot material of thick 55mm thereafter.King-sized defects i.e.cracks is failed to confirm in the surface of forge hot material.
Thereafter, if embody the surface flatness of forge hot material and remove slight surface blemish, the surface of this forge hot material is ground with grinder, obtain the forge hot material of thickness 53mm.
Then, use described forge hot to be heated to 1000 DEG C, carry out hot rolling with 1000 DEG C, obtain the hot rolling material of thick 1.7mm.Particularly defects i.e.cracks is failed to confirm in the surface of hot rolling material.
Subsequently, remove the oxide film thereon that is formed at described hot rolling material by pickling, use former material as cold rolling.The thickness of the former material of cold rolling use is 1.65mm.Use the described former material of cold rolling use to carry out cold rolling, obtain the cold rolling material of thick 0.8mm.The cold rolling material obtaining is finally annealed with 800 DEG C.Further, for fear of surface oxidation, use inactive gas atmosphere.
The cold rolling material that is associated gold from having carried out the Fe-Al of above-mentioned annealing extracts crystal grain and measures with test, confirms that crystal grain is that average crystal grain is the fine and uniform metal structure of 100 μ m.
Subsequently, in order to evaluate damping and amortization, use average crystal grain is the cold rolling material mensuration internal friction that the Fe-Al of 100 μ m is associated gold.The mensuration of internal friction is used the high-temperature elastic modulus synchronous measurement device that Japanese TECHNO-PLUS Co., Ltd. manufactures to measure internal friction.Consequently confirm at room temperature to obtain more than 0.1 internal friction, there is excellent damping and amortization.
Above, be associated golden manufacture method according to illustrated Fe-Al of the present invention, can effectively prevent from manufacturing time, there is crackle, and can manufacture thickness be below 0.8mm, there is the needed crystal grain Fe-Al of excellent damping and amortization and be associated golden cold-rolled strip.
Claims (4)
1. Fe-Al is associated a golden manufacture method, it is characterized in that, it possesses following operation:
Ingot manufacturing process, casting contains Al:2.0～9.0% in quality %, and the Fe-Al that surplus is made up of Fe and impurity is associated gold, and from mold, takes out and obtain ingot;
Hot forging process, ingot described in forge hot and become forge hot material;
Hot-rolled process, forge hot material described in hot rolling and become hot rolling material;
Oxide film thereon is removed operation, removes the oxide film thereon of described hot rolling material and becomes the cold rolling former material of using;
Cold rolling process, the former material of cold rolling described cold rolling use and become cold rolling material; And
Annealing operation, anneals for described cold rolling material,
In described ingot manufacturing process, be cooled to below before 250 DEG C in the surface temperature of the described ingot taking out from described mold, start the heating of the described ingot of described hot forging process.
2. Fe-Al according to claim 1 is associated golden manufacture method, it is characterized in that, described Fe-Al is associated gold and also contains l.0% following Nb in quality %.
3. Fe-Al according to claim 1 and 2 is associated golden manufacture method, it is characterized in that, surface temperature at the described ingot obtaining via described ingot manufacturing process was cooled to below before 250 DEG C, and after the ingot surface of the oxide film thereon through removing described ingot surface is removed operation, enter into described hot forging process.
4. be associated golden manufacture method according to the Fe-Al described in any one in claims 1 to 3, it is characterized in that, described annealing operation is carried out in non-oxidizing gas atmosphere.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2012084504 | 2012-04-03 | ||
| JP2012-084504 | 2012-04-03 | ||
| PCT/JP2013/059517 WO2013150972A1 (en) | 2012-04-03 | 2013-03-29 | Fe-Al ALLOY PRODUCTION METHOD |
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| CN104169027A true CN104169027A (en) | 2014-11-26 |
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| CN201380012914.3A Pending CN104169027A (en) | 2012-04-03 | 2013-03-29 | Fe-Al ALLOY PRODUCTION METHOD |
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|---|---|
| US (1) | US20140374050A1 (en) |
| JP (1) | JP6094576B2 (en) |
| CN (1) | CN104169027A (en) |
| TW (1) | TWI465584B (en) |
| WO (1) | WO2013150972A1 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111074175A (en) * | 2019-12-31 | 2020-04-28 | 江苏新华合金有限公司 | FeAl4 bar and production process thereof |
| 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 |
| CN114480982A (en) * | 2022-01-12 | 2022-05-13 | 沈阳工业大学 | Low-cost high magnetostriction coefficient Fe-Al based thin strip and preparation method thereof |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20170045833A1 (en) * | 2015-08-12 | 2017-02-16 | Fuji Xerox Co., Ltd. | Method for producing metal cylinder, method for producing substrate for electrophotographic photoconductor, method for manufacturing electrophotographic photoconductor, and metal slug for impact pressing |
| CN105522087A (en) * | 2016-01-19 | 2016-04-27 | 溧阳市金昆锻压有限公司 | Die forging process of granulator press roll |
| CN112729376A (en) * | 2020-11-27 | 2021-04-30 | 成都先进金属材料产业技术研究院有限公司 | Method for evaluating hot working performance of light high-strength steel |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09102408A (en) * | 1995-08-03 | 1997-04-15 | Nippon Steel Corp | Magnetic foil and its manufacture and high-frequency magnetic core using it |
| JP2001262221A (en) * | 2000-03-17 | 2001-09-26 | Asahi Tec Corp | Method for heating hot forging material |
| CN1346301A (en) * | 1999-02-09 | 2002-04-24 | 克里萨里斯技术公司 | Method of manufacturing metallic products such as sheet by cold working and flash annealing |
| CN1580328A (en) * | 2004-05-17 | 2005-02-16 | 文锐君 | Hot-rolling steel plate cleaning agent |
| CN101115850A (en) * | 2005-02-10 | 2008-01-30 | 大神田佳平 | Novel fe-al alloy and method for producing same |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2705353A (en) * | 1952-04-04 | 1955-04-05 | Kaiser Aluminium Chem Corp | Method of continuous casting |
| US3257835A (en) * | 1964-11-12 | 1966-06-28 | Southwire Co | Method of hot forming metal |
| JPH01289053A (en) * | 1988-05-16 | 1989-11-21 | Nippon Mining Co Ltd | Shadow mask |
| TW245661B (en) * | 1993-01-29 | 1995-04-21 | Hitachi Seisakusyo Kk | |
| JP4036449B2 (en) * | 2003-03-12 | 2008-01-23 | 川崎油工株式会社 | Scale removal equipment for billets for hot forging |
| JP2006239310A (en) * | 2005-03-07 | 2006-09-14 | Kahei Okanda | Golf club head, and golf club |
| EP2145027A1 (en) * | 2007-05-02 | 2010-01-20 | Corus Staal BV | Method for hot dip galvanising of ahss or uhss strip material, and such material |
| JP2010150615A (en) * | 2008-12-25 | 2010-07-08 | Kahei Okanda | Method for manufacturing surface-worked alloy and surface-worked alloy |
-
2013
- 2013-03-29 WO PCT/JP2013/059517 patent/WO2013150972A1/en active Application Filing
- 2013-03-29 JP JP2014509135A patent/JP6094576B2/en active Active
- 2013-03-29 CN CN201380012914.3A patent/CN104169027A/en active Pending
- 2013-04-01 TW TW102111619A patent/TWI465584B/en active
-
2014
- 2014-09-05 US US14/478,409 patent/US20140374050A1/en not_active Abandoned
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09102408A (en) * | 1995-08-03 | 1997-04-15 | Nippon Steel Corp | Magnetic foil and its manufacture and high-frequency magnetic core using it |
| CN1346301A (en) * | 1999-02-09 | 2002-04-24 | 克里萨里斯技术公司 | Method of manufacturing metallic products such as sheet by cold working and flash annealing |
| JP2001262221A (en) * | 2000-03-17 | 2001-09-26 | Asahi Tec Corp | Method for heating hot forging material |
| CN1580328A (en) * | 2004-05-17 | 2005-02-16 | 文锐君 | Hot-rolling steel plate cleaning agent |
| CN101115850A (en) * | 2005-02-10 | 2008-01-30 | 大神田佳平 | Novel fe-al alloy and method for producing same |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| CN113874140B (en) * | 2019-05-31 | 2023-08-29 | 株式会社博迈立铖 | Fe-Al alloy vibration-damping component and method for producing same |
| US11913097B2 (en) | 2019-05-31 | 2024-02-27 | Proterial, Ltd. | Fe—Al-based alloy vibration-damping component and method for manufacturing same |
| CN111074175A (en) * | 2019-12-31 | 2020-04-28 | 江苏新华合金有限公司 | FeAl4 bar and production process thereof |
| 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 |
| CN114480982A (en) * | 2022-01-12 | 2022-05-13 | 沈阳工业大学 | Low-cost high magnetostriction coefficient Fe-Al based thin strip and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6094576B2 (en) | 2017-03-15 |
| JPWO2013150972A1 (en) | 2015-12-17 |
| TW201348462A (en) | 2013-12-01 |
| WO2013150972A1 (en) | 2013-10-10 |
| US20140374050A1 (en) | 2014-12-25 |
| TWI465584B (en) | 2014-12-21 |
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