CN1767910A - A method for processing a steel product, and product produced using said method - Google Patents
A method for processing a steel product, and product produced using said method Download PDFInfo
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- CN1767910A CN1767910A CNA2004800086191A CN200480008619A CN1767910A CN 1767910 A CN1767910 A CN 1767910A CN A2004800086191 A CNA2004800086191 A CN A2004800086191A CN 200480008619 A CN200480008619 A CN 200480008619A CN 1767910 A CN1767910 A CN 1767910A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 254
- 239000010959 steel Substances 0.000 title claims abstract description 254
- 238000000034 method Methods 0.000 title claims abstract description 68
- 238000012545 processing Methods 0.000 title abstract description 18
- 238000005096 rolling process Methods 0.000 claims abstract description 90
- 230000002093 peripheral effect Effects 0.000 claims abstract description 17
- 238000009749 continuous casting Methods 0.000 claims description 32
- 238000001816 cooling Methods 0.000 claims description 20
- 239000000463 material Substances 0.000 claims description 20
- 238000004519 manufacturing process Methods 0.000 claims description 15
- 229910000859 α-Fe Inorganic materials 0.000 claims description 14
- 229910001209 Low-carbon steel Inorganic materials 0.000 claims description 11
- 238000005266 casting Methods 0.000 claims description 11
- 238000010438 heat treatment Methods 0.000 claims description 10
- 229910052751 metal Inorganic materials 0.000 claims description 10
- 239000002184 metal Substances 0.000 claims description 10
- 229910001220 stainless steel Inorganic materials 0.000 claims description 10
- 239000010935 stainless steel Substances 0.000 claims description 9
- 239000000956 alloy Substances 0.000 claims description 7
- 238000000137 annealing Methods 0.000 claims description 7
- 239000010936 titanium Substances 0.000 claims description 7
- 229910052719 titanium Inorganic materials 0.000 claims description 7
- 229910000922 High-strength low-alloy steel Inorganic materials 0.000 claims description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 6
- 229910045601 alloy Inorganic materials 0.000 claims description 6
- 229910052796 boron Inorganic materials 0.000 claims description 5
- 230000003247 decreasing effect Effects 0.000 claims description 5
- 239000010955 niobium Substances 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 5
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 4
- 229910000734 martensite Inorganic materials 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 4
- 238000011282 treatment Methods 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 2
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 239000004411 aluminium Substances 0.000 claims description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 2
- 229910001563 bainite Inorganic materials 0.000 claims description 2
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 239000010949 copper Substances 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 2
- 239000000047 product Substances 0.000 description 27
- 239000002131 composite material Substances 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 239000002245 particle Substances 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 238000002425 crystallisation Methods 0.000 description 5
- 230000008025 crystallization Effects 0.000 description 5
- 238000005520 cutting process Methods 0.000 description 5
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 238000010008 shearing Methods 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000010276 construction Methods 0.000 description 3
- 230000006378 damage Effects 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 239000007795 chemical reaction product Substances 0.000 description 2
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 230000007812 deficiency Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000004080 punching Methods 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- 229910000617 Mangalloy Inorganic materials 0.000 description 1
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 239000002360 explosive Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000007429 general method Methods 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000011005 laboratory method Methods 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000010310 metallurgical process Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000012805 post-processing Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
- B21B1/026—Rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/16—Control of thickness, width, diameter or other transverse dimensions
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
- B21B2001/383—Cladded or coated products
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2267/00—Roll parameters
- B21B2267/02—Roll dimensions
- B21B2267/06—Roll diameter
- B21B2267/065—Top and bottom roll have different diameters; Asymmetrical rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2275/00—Mill drive parameters
- B21B2275/02—Speed
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2275/00—Mill drive parameters
- B21B2275/02—Speed
- B21B2275/04—Roll speed
- B21B2275/05—Speed difference between top and bottom rolls
-
- 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
-
- 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
-
- 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
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Electrical Discharge Machining, Electrochemical Machining, And Combined Machining (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
The invention relates to a method for processing a steel product, in which the steel product is passed between a set of rotating rolls of a rolling mill stand in order to roll the steel product. According to the invention, the rolls of the rolling mill stand have different peripheral velocities such that one roll is a faster moving roll and the other roll is a slower moving roll, and the peripheral velocity of the faster moving roll is at least 5% higher and at most 100% higher than that of the slower moving roll, and the thickness of the steel product is reduced by at most 15% per pass, and the rolling takes place at a maximum temperature of 1350 DEG C. The invention also relates to a steel product produced using the method, and to the use of this steel product.
Description
Technical field
The present invention relates to a kind of method of handling steel part, in the method, steel part is by between one group of rotary roller of rolling-mill housing.This rolling-mill housing can be the part of rolling equipment, and rolling equipment is made up of one or more rolling-mill housing.
Background technology
Rolling is a kind of operation of very standard, and it can give general metal (especially steel) desirable size and performance.Except steel part is obtained the desirable final geometry, because metallurgical process takes place in when rolling and rolling back, therefore the rolling structure that also can make makes moderate progress.
But, for wide product, it has been generally acknowledged that traditional rolling be a plane strain compression process, can cause sizable varied in thickness, in some cases, this point is undesirable or impossible.For example, in heavy construction, when especially producing offshore work platform or bridge, must use the thick steel plate of 60-150mm.At present, because the maximum ga(u)ge of cast steel plate is less than 400mm, only be equivalent to about 60% and be rolled down to the varied in thickness that 150mm causes.Usually can cause the varied in thickness of 10-30% by each passage of traditional roll stand.
Cause forming loose structure when steel plate is cast with, this characteristic is that casting process is intrinsic.Because the number of times of steel plate rolling is abundant, the pressure that this loose structure will be applied in is closed.But, if must form very thick plate, then rollingly only can close the outermost hole of steel plate, and can not close those holes of material heart portion.But, the hole of these material heart portions is very unfavorable to the toughness of the mechanical performance of material, especially plate.Grain refinement also occurs over just the outermost layer of plate.For the pass closed pore of exerting pressure, and in order to realize the grain refinement center of plate (or even), so the rolling degree of steel plate must be higher, yet the initial thickness of steel plate and the final thickness of steel part are combined, and do not allow thickness significantly to reduce usually.
Using under the small sample laboratory condition, a big equivalent strain can be incorporated in the product and thickness is significantly reduced with equal channel angular extruding (ECAE) method, the equal channel angular pressing method can not change the size of sample and make it produce great shear strain.In the equal channel angular pressing method, make billet (billet) by punching block with being squeezed, punching block has the passage that two cross sections equate and intersect at an angle.Under ideal conditions, when passing the intersection plane of two passages, billet is sheared, and shearing displacement is determined by the angle between two passages.In this course,, therefore this process can be repeated, strain can be gathered like this because cross section does not change.But, owing to need very high operating force, and this technology can not be risen to the flat product that adapts to stock size, therefore this laboratory technique can not be applied in the industrial production of steel part.
Summary of the invention
Therefore, one object of the present invention is to provide a kind of method, and it can be incorporated into big equivalent strain in the steel part and can not make product thickness produce identical reducing.
One of purpose of the present invention also is to provide a kind of method of handling steel part, and it can make the performance of the product of production make moderate progress.
Another object of the present invention also is to provide a kind of method of handling steel part, and it can make the product grains refinement of its production.
Another object of the present invention also is to provide a kind of method of handling continuous casting steel machine, and this method can be improved the performance of steel plate or band.
Another object of the present invention is to provide a kind of method of handling continuous casting steel billet or wire rod, this method can be closed the hole of founding materials.
The steel part that another object of the present invention also is to provide a kind of mechanical performance to improve, this steel part utilizes this method to produce.
The specific embodiment
In the present invention, should think that ladle draws together all ferroalloys, for example ultra-low-carbon steel, mild steel, in to high-carbon steel, electrical steel and stainless steel.Steel part among the present invention comprises steel ingot, steel plate, steel bloom, billet, bar, steel bar, wire rod and section bar.
The method of handling the continuous casting steel machine product can reach one or more in these purposes, in the method, for the rolled steel goods, steel passes through between a cover rotary roller of roll stand, wherein, the roll of roll stand has different peripheral speeds, make that a roll is the quick rotation roller, another roll is the slow rotation roller, and wherein, the peripheral speed of quick rotation roller is than the peripheral speed height at least 5% of slow rotation roller, at the most 100%, for each passage, it is many 15% that the thickness of steel part is decreased to, and the maximum temperature of rolling generation is 1350 ℃.
Because roll has different peripheral speeds, so shearing can occur in the steel part, and has been found that on the whole thickness of product and all can take place.Have been found that this needs at least 5% speed difference.Shearing can cause bore closure to a very big degree of continuous casting material.This does not need very big varied in thickness, and 15% varied in thickness just can make bore closure at the most.The decrease of thickness is preferably at the most 8%, and more preferably at the most 5%.This is highly beneficial in the process of handling those steel part, owing to will keep thickness substantially, therefore when handling beginning, the size of steel part does not allow significantly to reduce on thickness direction.
In addition, the rolling grain refinement that causes importantly of the present invention, grain refinement occur on the whole thickness of rolling stock, and this mechanical performance to steel plate or wire rod is favourable.In addition, the intensity of material increases.The useful influence of less crystallite dimension is known.
Rollingly preferably at high temperature carry out.But, owing to will avoid on the surface of the steel part that is about to produce, forming the eutectic oxide, so maximum temperature is limited in 1350 ℃.High temperature can make and rollingly move more steadily.
Wish also that processing of the present invention can be produced and spread less rolled sheet.
Preferably, the peripheral speed of quick rotation roller is more preferably up to many 20% than the peripheral speed height of slow rotation roller at the most 50%.If the speed difference between the roll is very big, between roll and steel part, just have very big slip danger so, this can cause shearing inhomogeneous.
According to useful embodiment, rolling mill so designs, and promptly roll has different diameters.Can obtain desirable difference like this.
According to another useful embodiment, roll has different rotary speeies, and it is poor that this also can obtain desirable rotary speed.
In order to obtain the desirable difference of roll, can be with back two kinds of methods---be that the roll of different-diameter and the roll of different rotation rates combine.
According to a preferred embodiment of this method, become the angle between 5-45 ° that steel part is introduced between the roll with the relative vertical line on the plane by the roll central axis.Steel part introduced between the roll can make roll more easily clamp steel part with certain angle, so can make the variation of thickness can keep low as much as possible.Test shows that also if with certain angle steel part is introduced between the roll, the glacing flatness of so rolling back steel part increases.Steel part is preferably introduced with the angle between 10-25 °, more preferably the angle between 15-25 °.Because with such angle, steel part can come out from milling train with the glacing flatness of high level.Decrease, steel part and types of alloys and the temperature of steel part size also depended in the influence that should be noted that the latter.
For this purpose, after the rolling intact first time, handle that operation preferably repeats 1 time again or repeatedly.For example, enough good grain refinement can obtain for 3 times by carrying out processing operation of the present invention.But, handle the number of times of operating execution and depend on the thickness of steel part, the difference and the desirable grain refinement of roll.Handling in the operation each time, hope is introduced steel part between the roll with the angle between 5-45 °, preferably between 10-25 °, more preferably between 15-25 °.
If processing procedure of the present invention can repeat repeatedly, in a preferred embodiment, for each passage, steel part can pass through roll stand with opposite direction.After each then rolling operation, steel part can change direction, always by same roll stand.In this case, for each passage, roll must rotate in the opposite direction.Also be in this case, wish that the steel part under every kind of situation all is incorporated between the roll with certain angle.
In a further advantageous embodiment, steel part is successively by 2 or a plurality of roll stand.This method mainly is fit to band, and band can promptly carry out desirable processing operation by this way.
In a preferred embodiment of the invention, steel part is rolled, this steel part top layer at least is essentially austenitic structure, is essentially austenitic structure on the preferred whole steel part.800-870 ℃ (certainly depend on chemical composition) of typical minimum temperature scope from 900 ℃ of ultra-low-carbon steel to mild steel is to about 723 ℃ of the steel that contains 0.8% carbon.In all cases, maximum temperature is 1350 ℃.When rolling austenitic stainless steel, rollingly always occur on the austenitic structure.
In second preferred embodiment, steel part is rolled, this steel part top layer at least has the two phase structure that is essentially austenite-ferrite, on the preferred whole steel part two phase structure that is essentially austenite-ferrite is arranged.For mild steel, typical temperature range is with 800-870 ℃ of end since 723 ℃.Along with carbon content increases, temperature range reduces gradually to drop to the eutectoid point of about 723 ℃ (steel that contain 0.8% carbon).
In the 3rd preferred embodiment, steel part is rolled, this steel part top layer at least is essentially ferritic structure, is essentially ferritic structure on the preferred whole steel part.Be higher than 0.02% mild steel for carbon content, maximum temperature is approximately 723 ℃, and for the steel (as ultra-low-carbon steel) of low carbon content, maximum temperature is approximately 850 ℃.These temperature limits that are noted that ferrite, ferritic-austenitic and austenitic area here depend on that the heat machinery of the composition of steel and steel is historical.In case surpass critical-temperature, phase transformation just is not to take place moment, so compare with the intermediate layer of steel part, the phase transformation steel can have an out of phase top layer.
In another preferred embodiment of the present invention, rollingly between 0-720 ℃, carry out.This not only comprises the cold rolling of ferritic steel product, but also comprises the preferably rolling of martensitic structure or austenite stainless steel construction.
Making before and after the rolling operation that utilizes rolling mill to carry out is possible in this way, and the roll of rolling mill has essentially identical peripheral speed.Like this, with this embodiment, can accurately give desirable thickness of product or smoothness.
In a further advantageous embodiment, the method for production steel part comprises the steps:
The continuous casting continuous casting steel billet;
Selectively heat the continuous casting steel billet between casting machine and the steel rolling equipment and/or make its temperature even;
Rolled steel goods in one or more roll stands of rolling equipment selectively, rolling equipment has the essentially identical roll of peripheral speed;
After last once rolling step, selectively quicken cooling;
In rolling front and back, selectively steel part is cut into steel plate or coiled material;
Selectively coil steel part;
The cooling steel part.
The most general method of producing steel plate is the continuous casting continuous casting steel billet, is cut to the steel plate of thickness between 200-400mm.After the casting, before these steel plates are incorporated into the hot strip mill heating furnace, need it is cooled to environment temperature.In some cases, when the steel plate of casting is still warm or warm, it can be incorporated in the heating furnace and (be called " hot charging " or " directly charging ").
The thickness of continuous casting steel billet preferably is lower than 150mm, when sheet metal is cast, and more preferably less than 100mm, even more preferably less than 80mm.
Can cut continuous casting steel billet with cutting equipment after the casting.So the steel plate that obtains can be preserved the processing in order to the back, makes its cooling, perhaps handles immediately.In the previous case, steel plate needs to heat once more before rolling, and under latter event, steel plate needs temperature even.Finish rolling after, rolling product can make its cooling with quickening cooling, selectively coils.After last processing step, steel product cools or be cooled to environment temperature.If continuous casting steel billet is not cut into steel plate, but carry out continuous, processing without a head or semi-endless rolled immediately, rolling product will be in the last stages cutting of the operation of rolling, before for example optional coiling machine.Clearly, of the present inventionly rollingly occur between casting step and the last cooling step or even afterwards Anywhere.
Before coiling, steel part may be subjected to quicken cooling.After last processing step, steel product cools or be cooled to environment temperature.
In another embodiment of the present invention, the thickness of continuous casting steel billet preferably is lower than 20mm, more preferably less than 10mm with even more preferably less than 5mm.
After casting, the continuous casting steel billet that can have cast microstructure with cutting equipment cutting.So the steel plate that obtains can be preserved in order to post processing, makes its cooling, perhaps can handle these steel plates immediately.In the previous case, before rolling, steel plate may need to heat once more, and perhaps they can be used as finished product.Under latter event, steel plate may need temperature even.A shortcoming of band cast steel goods is that final products still have cast microstructure to a great extent, and this is because band almost is not rolled.Thereby the mechanical performance of end product is relatively poor relatively, so the purposes of end product is restricted, can not satisfy with traditional steel plate or even the standard of the product that obtains of nearest sheet metal method.In the operation of rolling of the present invention, microstructure is converted to the forging microstructure and does not reduce thickness basically from cast structure, improves the final performance of steel part widely with this.Finish rolling after, rolling product can cool off with quickening, and selectively coils.After last processing step, steel product cools or be cooled to environment temperature.If continuous casting steel billet is not cut into steel plate, but immediately by continuous, without a head or half rolling processing without a head, rolling product will be in the last stages cutting of the operation of rolling, for example before optional coiling machine.Finish rolling after, rolling product can cool off with quickening.After last processing step, steel product cools or be cooled to environment temperature.In addition, clearly, rolling can occurring between casting step and the last cooling step of the present invention, perhaps even afterwards Anywhere.
If the steel part of handling according to preceding two embodiment is a stainless steel, can obtain other benefit.
In the present invention, stainless steel comprises ferrite, austenite-ferrite duplex steel and austenitic stainless steel.These steel are used in the occasion of the corrosion resistance deficiency of non-alloy or low-alloy steel usually.Corrosion-resistant, high strength is relevant with the duplex alloy stainless steel usually with good ductility, the combine occasion of the formability deficiency that can be used on ferrite and austenitic stainless steel of three.Exemplary according to the ferritic stainless steel of EN10088 (1995) is X2CrNi12-1.4003 (410) X6Cr14-1.4016 (430), and the exemplary of austenitic stainless steel is X5CrNiMo17-12-21.4401 (316) X5CrNi18-10-1.4301 (304).Generally speaking, these steel are used on sheet material, band, semi-, steel bar, the bar as general stainless steel, and as the part of construction(al)steel, pipeline, kitchen utensils, pump and valve etc.
The thickness of each passage steel plate or band preferably be decreased to many 15% and more preferably each passage be decreased to many 8% and more preferably each passage at the most 5%.Owing to shear,, obtain the thickness that grain refinement can not need to reduce material so the difference between the roll can cause grain refinement.Reducing thickness mainly is in order to make the roll fastening material.This only needs very little varied in thickness, and this is favourable to thin continuous casting steel plate, Strip casting material and band.After each passage, decrease is more little, and it is thick more that steel plate or band keep.So, continuous casting steel plate and band may use increase.Utilize method of the present invention, can give steel part better mechanical performance, and not need to reduce thickness basically.Because method of the present invention can be used for giving relatively thin steel part more performance, the thicker continuous casting plate and the band of mechanical performance also obtain commercial Application so wish to have preferably.
(these steel grades are commonly referred to the HSLA steel to contain the high strength microalloy steel band of one or more element nbs, V, Ti or B in production, be Aldecor) time, in hot strip mill, according to the principle of well-known thermomechanical rolling, the steel of producing big thickness is inconvenient.The fixed thickness of continuous casting steel plate that is used to begin the operation of rolling usually between 200-350mm, 225mm for example.Usually rolling mill also is divided into the roughing part, and the many passages of steel plate rolling (for example 5 passages) reach selected thickness, for example 36mm herein.Usually the thickness of this so-called drive link (transfer bar) is fixed in specific hot strip mill, and is minimum with the deviation of this fixed value.Increase this value and can produce deviation with this fixed value, this can produce roll-force or the moment of torsion that surpasses the operation restriction usually on finishing mill, thereby jeopardizes rolling mill or cause the shape of product and profile to become and can not accept.The thickness that reduces drive link can cause surpassing the roll-force or the moment of torsion of the roughing mill that moves restriction usually.But, the fixed value of drive link also produces a problem because it can cause thick steel band (as 18mm) and thin steel band (for example 4mm) to reduce value different.Under first kind of situation, total decrease of finishing mill is that 50%, the second kind of situation is 89%.During the hot rolling and after the hot rolling, this microstructural development to steel has very big influence, and this is because thermodynamic condition differs widely, and this can cause the crystallization again of deformed austenite different different with the precipitation kinetics of microalloy element.Thereby in the cooling procedure after rolling, phase transformation also is affected.In a preferred embodiment of the invention, do not need to increase the deformation extent that transfer bar thickness can improve steel part, perhaps when the final thickness of steel part increases, can keep deformation extent constant.
With regard to section bar, deformation extent also is important to the performance of final products.For example, know, the billet that is rolled into section bar (for example I-steel) usually some almost do not pass through any rolling, so grain refinement seldom or not takes place in this part.The cross section specification of billet usually between 200-400mm, for example 230mm or 310mm.In steel plate/steel bloom/billet stage, after being heated to the highest 1350 ℃ again, they are rolled.Finish rolling is that austenite and edge thickness take place under the temperature between the 10-150mm at steel usually.The nonrestrictive example that is used as the typical steel grade of these section bars comprises CMn steel and HSLA steel.Because the deformation extent of billet is bigger, processing therefore of the present invention allows billet that thinner crystallite dimension is arranged, and also can reduce the size in the hole of billet, thereby can produce better fracture toughness.
Recently the basic research result shows, can improve performance such as intensity, toughness and corrosion resistance by reducing crystallite dimension.By the structure of control crystal grain, developed the very tiny steel of crystallite dimension.Compare with conventional steel, these steel not only provide higher tensile strength, also can improve toughness, durability and corrosion resistance.Roll-force and moment of torsion reduce by under low rolling temperature, producing very big thickness, and this technology be applied in the hot strip mill, so can be brought up to high level.But, the scheme of the acquisition ultra-fine ferrite crystal grain of proposition depends under low hot rolling temperature the grain refinement of being undertaken by generally rolling (being the plane strain compression), and strong rolling mill of needs.And, material is applied strong thickness reduce to obtain desirable deformation level.In processing of the present invention since in steel the gathering of strain, so crystal grain can reduce in a large number, and thickness does not reduce basically.The average grain size of the steel part that obtains is more preferably less than 2 μ m, even is more preferably less than 1 μ m preferably less than 5 μ m.
According to another embodiment of the present invention since in steel the gathering of strain, so the performance of complex phase steel can unexpectedly improve, and thickness does not reduce basically.When steel part is rolled and quickens to cool off subsequently, very big gather the equally distributed particulate time looks that deformation extent makes steel be transformed into very tiny ferrite crystal grain and be made up of bainite or martensite under austenitic state.Also there is minor amount of carbide.The ferrite content of this steel part preferably at least 60%, more preferably at least 70%, even more preferably at least 80%.The average grain size of the steel part that obtains is more preferably less than 2 μ m, even is more preferably less than 1 μ m preferably less than 5 μ m.
In the traditional mode of production of steel plate (for example carbon manganese shaped steel plate or HSLA shaped steel plate), starting point is the continuous casting steel plate with common thickness (between the 200-350mm).These steel plates can be heated between 1000-1350 ℃ in reheating furnace again.After the heating, these steel plates are rolled into the thickness between the 30-200mm again, the thickness between the preferred 40-150mm, and remain on a certain temperature, for example by shielding in case cooling keep.Keep the phase at high temperature, because grain growth takes place, the final mechanical performance of last steel plate is possible deviation also.Well-known bigger crystallite dimension reduces the ductility and the toughness of steel part.It also is well-known that yield strength reduces along with the increase of crystallite dimension.Thereby, should avoid grain growth in the maintenance phase.As a rule can avoid by quickening cooling.But, use the adverse effect of quickening cooling to be to make the core of steel plate and the temperature difference between the surface portion to increase.This temperature difference has a negative impact to the final microstructural uniformity of steel plate.
In many cases, accept heat treatment at the production technology light plate.Normalized treatment for example, its light plate is reheated into the austenitic area, and allows it to cool off in still air or in temper annealing or in stress relieving annealing, and their purpose all is to reduce the level of internal stress.Heat treated another example is that nodularization (speroidisation) is handled, and in the reason, elongated carbide is transformed into spheric granules more or less herein.These carbide can be the carbide (for example cementite) of iron or the carbide (as chromium carbide) of other metal.Such annealing in process is used in carbon content usually and is higher than on 0.8% the steel.Unfortunately, most these heat treatments, especially spheroidising need for a long time, often cause the decarburization of strip surface part, can influence its performance conversely thus.
Of the present invention rollingly also can under the low temperature between 0-720 ℃, carry out.When moving (promptly cold rolling) at low temperatures,, therefore be expected to obtain rolling particular advantage owing to destroyed unwanted particle.Because the destruction of particle, the final performance of steel part increases.The failure by shear that the operation of rolling produces the particle in the steel part, metal carbides (as cementite or chromium carbide) for example, this can improve toughness.The destruction of particle also influences the heat treatment response of steel part.Can adopt different heating and cooling modes, the output the processing stage that this can improving heat treatment stages, for example spheroidizing, the product that perhaps is improved.
Method of the present invention also can be carried out before or after the heat treatment of steel part.These heat treated examples are that well-known normalized treatment, stress relieving annealing processing, temper annealing processing or spheroidizing are handled.
In the present invention, steel part also comprises a kind of like this steel, promptly of the present invention rolling before, be about to cover one or more layers on the rolling steel surface at one or two.The combination that is coated with the steel part of one or more layers metal on one or two surface is commonly called composite plate or band.When the production composite plate, there are three kinds of methods metal covering can be attached on the steel substrate, i.e. explosive welding, roll bonding and built-up welding (weld overlay).A key factor that influences the composite plate quality is the bonding quality between base material and the composite bed.This is the particular challenge of the roll bonding composite plate of producing, this be because in tradition is rolling between base material and the composite bed or the stress state at the interface between the composite bed have only pressure.In a preferred embodiment, before rolling, be about to the surface coverage last layer or the multilayer of rolling steel part.Cover layer can be a kind of metal, preferred other steel, and for example the steel or stainless steel of heterogeneity wherein contains titanium, nickel, copper, aluminium or alloy.Like this, it is possible for example producing stratified material, and stratified material for example is used in as the composite material in pipe and pipe-line system, chemical plant, power plant, container, the pressure vessel.
The present invention also relates to a kind of by the metallic plate or the band that cast the improvement of producing continuously, the preferred method of using first aspect present invention, metallic plate or band center Kongzui large scale are less than 200 μ m in the method, preferably less than 100 μ m, be more preferably less than 20 μ m, even be more preferably less than 10 μ m.Because continuous casting, continuous casting plate and band always have remarkable hole greater than 200 μ m.The rolling operation of standard only can be closed the hole of these centers or can not be closed at all on not half.Rolling operation of the present invention can provide very little continuous casting plate in hole and band.
The present invention also relates to a kind of metallic plate or band that casts the improvement of production continuously, preferably use the method for first aspect present invention, in the method, the whole thickness of metallic plate or band is having substantially uniformly crystallization degree again after the crystallization again.Because rolling operation of the present invention, the fact that all crystal grains (comprise center those) is all sheared means continuous casting plate and band crystallization again on whole thickness.
The present invention also relates to steel part produced according to the invention, preferably its thickness is between 10-300mm, and more preferably between 20-160mm, for example 60mm for example is used in building, bridge, earth-moving equipment, pipeline, shipbuilding industry and the off-shore structure.
The present invention also relates to billet produced according to the invention, for example as the raw material of producing shaped steel, for example I-steel.
The present invention also relates to steel part produced according to the invention, wherein, starting point is a steel ingot, the hole preferred maximum dimension of the center of product is less than 200 μ m in this steel part, be more preferably less than 100 μ m, further preferably less than 20 μ m, even be more preferably less than 10 μ m, steel part according to continuous casting of the present invention and process for producing also is like this, the Kongzui large scale of the center of metallic plate or band is less than 200 μ m, be more preferably less than 100 μ m,, even be more preferably less than 10 μ m further preferably less than 20 μ m.
The present invention also relates to steel band produced according to the invention, for example, be used in the part of automobile, transporting equipment, piling, building, framework and for example be used in the clad steel goods and the steel band of pipe, chemical plant, power plant, container, pressure vessel, wherein, steel is the HSLA steel, comprises at least a in niobium, titanium, vanadium or the boron element or a kind of ultra-low-carbon steel, preferred partially stabilized at least steel preferably has at least a in titanium, niobium or the boron element.
Explain the present invention below with reference to exemplary embodiment.
Steel plate with a kind of stable ultra-low-carbon steel, carbon manganese steel and niobium micro-alloy HSLA steel of titaniferous is tested.
Steel plate is introduced with different angle (changing between 5-45 °).When they were incorporated into steel rolling equipment, the temperature of steel plate was approximately 1000 ℃.Two rolls are driven with the speed that per minute 5 changes.
Rolling back steel plate has certain curvature, and this depends primarily on the angle of introducing.The glacing flatness of rolling back steel plate is to a great extent by the angle decision of introducing, and in this case, optimum introducing angle depends on the type that reduces degree, material and alloy and the temperature of steel plate.For steel plate rolling in the above-mentioned test, optimum introducing angle approximately is 20 °.
The angle of shear according to steel plate rolling in the above-mentioned test is 20 °.With the decrease of this tolerance and steel plate, can calculate equivalent strain with following formula.
This formula can be used for representing the strain on the one dimension, derives from " Fundamental ofmetal forming " (metal forming basic principle) book (R.H.Wagoner and J.L.Chenot, John Wiley and Sons published in 1997).
So in according to the rolling steel plate of this test, equivalent strain is
In common rolling mill rolling, on the thickness of steel plate, do not shear, so equivalent strain just
(serves as that basic whole thickness to steel part calculates with uniform strain)
So with the rolling generation equivalent strain of method of the present invention, it is than with the rolling high 3-4 of equivalent strain of tradition doubly, and without any difference.In steel plate, high equivalent strain means less porosity rate, more crystallization again, thereby the inferior looks particle (composition particle) of good grain refinement and more extensive destruction is arranged.If equivalent strain improves, in general, the technical staff in engineering field knows these influences.So owing to use the method according to this invention, the rolling performance of material that means according to the present invention has greatly improved.
Claims (32)
1. method of handling steel part, wherein, for the rolled steel goods, steel part is passed through between one group of rotary roller of roll stand, it is characterized in that: the roll of roll stand has different peripheral speeds, makes that a roll is the quick rotation roller, and another roll is the slow rotation roller; The peripheral speed of quick rotation roller is than the peripheral speed height at least 5% of slow rotation roller, at the most 100%; The thickness of each passage steel part is decreased to many 15%; And rollingly when being 1350 ℃, maximum temperature carries out.
2. the method for claim 1 is characterized in that, it is many 8% that the thickness of each passage steel part is decreased to, preferably at the most 5%.
3. method as claimed in claim 1 or 2 is characterized in that, the peripheral speed of quick rotation roller is preferably up to many 20% than the peripheral speed height of slow rotation roller at the most 50%.
4. the described method of one of claim as the aforementioned is characterized in that, rolling mill is designed to roll has different diameters.
5. the described method of one of claim as the aforementioned is characterized in that roll has different rotary speeies.
6. the described method of one of claim as the aforementioned, it is characterized in that, become the angle between 5-45 ° that steel part is introduced between the roll with the relative vertical line on the plane by the roll central axis, preferably with the angle between 10-25 °, more preferably with the angle between 15-25 °.
7. the described method of one of claim as the aforementioned is characterized in that, carry out the first time rolling after, repeat the rolling operation of one or many.
8. method as claimed in claim 7 is characterized in that, each passage steel part all passes through roll stand with opposite direction.
9. method as claimed in claim 7 is characterized in that, steel part is successively by two or more roll stands.
10. the described method of one of claim as the aforementioned is characterized in that the described rolling operation of one of claim 1-9 can be carried out before or after the rolling operation of carrying out with rolling mill, and each roll has essentially identical peripheral speed in rolling mill.
11., it is characterized in that the steel part that top layer is at least had the austenitic structure of being essentially is rolled as each described method among the claim 1-10, preferably, be that the steel part of austenitic structure is rolled basically fully to having.
12. as each described method among the claim 1-10, it is characterized in that, at least top layer being had the steel part that is essentially the austenite-ferrite two phase structure be rolled, preferably, is that the steel part of austenite-ferrite two phase structure is rolled to having basically fully.
13., it is characterized in that top layer at least being had the steel part that is essentially ferrite structure be rolled as each described method among the claim 1-10, preferably, be that the steel part of ferrite structure is rolled basically fully to having.
14. as each described method among the claim 1-10, it is characterized in that, when the temperature of steel part is higher than 0 ℃, is rolled when being lower than 720 ℃.
15. method as claimed in claim 14 is characterized in that, is rolled having the steel part that is essentially martensitic structure.
16. a method of producing steel part, it may further comprise the steps:
The continuous casting continuous casting steel billet;
Selectively heat the continuous casting steel billet between casting machine and the rolling equipment, and/or make its temperature even;
Rolled steel goods selectively on one or more rolling-mill housing of rolling equipment, the roll of this rolling equipment has essentially identical peripheral speed;
After last once rolling step, selectively quicken cooling;
Before or after rolling, selectively steel part is cut into steel plate or coiled material;
Coil steel part selectively;
The cooling steel part;
It is characterized in that,, or after cooling, handle steel part with arbitrary method of claim 1-10 at the casting continuous casting steel billet with between quickening cooling or coiling or cool off.
17. the method for production steel part as claimed in claim 16 is characterized in that, the thickness of continuous casting steel billet is lower than 150mm, preferably is lower than 100mm, more preferably less than 80mm.
18. the method for production steel part as claimed in claim 16 is characterized in that, the thickness of continuous casting steel billet is lower than 20mm, preferably is lower than 10mm, more preferably less than 5mm.
19., it is characterized in that the steel part of production is a stainless steel product as the described method of claim 16-18.
20. the method as the described production steel part of claim 16-19 is characterized in that, the steel part with the austenitic structure of being essentially is rolled, and then steel is quickened cooling; Steel part mainly comprises ferrite, bainite and/or martensite, and the ferritic content in cooling back preferably is at least 60%, more preferably more than 70%, even more preferably more than 80%.
21. the method as the described production steel part of claim 16-20 is characterized in that, the average grain size of steel part preferably less than 2 μ m, is more preferably less than 1 μ m less than 5 μ m.
22. as each described method among the claim 1-21, it is characterized in that steel part was subjected to heat treatment before or after rolling step, for example normalized treatment, full annealing, stress relieving annealing or spheroidizing are handled.
23., it is characterized in that the surface of the steel part that will be rolled covers last layer or multilayer as each described method among the claim 1-21 before rolling.
24. method as claimed in claim 23 is characterized in that cover layer is a metal, is preferably another kind of steel, as has the steel or stainless steel of heterogeneity, wherein contains titanium, nickel, copper, aluminium or alloy.
25. the steel part that each described method is produced in the claim as described above, its thickness is preferably between 10-300mm, between 20-160mm, for example be 60mm more preferably, for example can be used on building, bridge, earth-moving equipment, pipeline, shipbuilding industry and the off-shore structure.
26. the steel part as each described method among the claim 1-24 is produced is characterized in that steel part is a billet.
27. a shaped steel, for example I-steel is characterized in that, shaped steel is produced with the described billet of claim 26.
28. the steel part as each described method among the claim 1-24 is produced is characterized in that starting point is a steel ingot, in steel part, the full-size in the center hole is more preferably less than 100 μ m preferably less than 200 μ m, further preferably less than 20 μ m, even be more preferably less than 10 μ m.
29. with steel plate, band or the billet of the described method of one of claim 1-10 by continuous casting production, it is characterized in that, the full-size in the hole, center of sheet material, band or billet is preferably less than 200 μ m, be more preferably less than 100 μ m, further preferably less than 20 μ m, even be more preferably less than 10 μ m.
30. the steel band as method as described in one of claim 16-21 is produced for example is used on the part of automobile, transporting equipment, piling, building, framework.
31. the clad steel goods as claim 23 or 24 described methods productions for example are used on pipeline, chemical plant, power plant, container, the pressure vessel.
32. the steel band that produces as claim 16,17,18 or 21 described methods, it is characterized in that, described steel is the HSLA steel, it comprises at least a in niobium, titanium, vanadium or the boron element, perhaps described steel is a ultra-low-carbon steel, be preferably partially stabilized at least ultra-low-carbon steel, more preferably have at least a in titanium, niobium or the boron element.
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| EP03075546.6 | 2003-02-24 | ||
| EP03075546A EP1449596A1 (en) | 2003-02-24 | 2003-02-24 | A method for processing a steel product, and product produced using said method |
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| CN1767910A true CN1767910A (en) | 2006-05-03 |
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| US (1) | US20070051439A1 (en) |
| EP (2) | EP1449596A1 (en) |
| JP (1) | JP2006520692A (en) |
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| CN102154537A (en) * | 2011-02-14 | 2011-08-17 | 南京润邦金属复合材料有限公司 | Composite carbon tool steel/plain carbon steel metallurgical lining board with high resistance, high uniformity and long service life |
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| NL1018815C2 (en) * | 2001-08-24 | 2003-02-25 | Corus Technology B V | Method for processing a metal slab or billet, and product made with it. |
| KR20070099684A (en) | 2005-02-02 | 2007-10-09 | 코루스 스타알 베.뷔. | Austenitic steel having high strength and formability, method of producing said steel and use thereof |
| DK2189174T3 (en) | 2005-09-26 | 2013-03-04 | Univ Leeds | METHOD OF ADMINISTRATING MEDICINE |
| JP5221348B2 (en) * | 2006-07-27 | 2013-06-26 | 国立大学法人 東京大学 | Multi-layer steel and method for producing multi-layer steel |
| WO2009135514A1 (en) * | 2008-05-09 | 2009-11-12 | Ady Palti | Surgical tool, especially for machining bones for insertion of a dental implant |
| US8522471B2 (en) * | 2010-06-25 | 2013-09-03 | Pacific Aerospace & Electronics, Inc. | Firearms and firearm components comprising bonded multi-metallic materials; methods of manufacture |
| KR101230139B1 (en) * | 2010-12-28 | 2013-02-05 | 주식회사 포스코 | continuous cold rolling method of stainless steel |
| KR101342487B1 (en) | 2011-06-29 | 2013-12-17 | 포항공과대학교 산학협력단 | Method for manufacturing steel plate with a layered structure |
| JP5382257B1 (en) * | 2013-01-10 | 2014-01-08 | 大日本印刷株式会社 | Metal plate, method for producing metal plate, and method for producing vapor deposition mask using metal plate |
| JP5455099B1 (en) | 2013-09-13 | 2014-03-26 | 大日本印刷株式会社 | Metal plate, metal plate manufacturing method, and mask manufacturing method using metal plate |
| JP5516816B1 (en) * | 2013-10-15 | 2014-06-11 | 大日本印刷株式会社 | Metal plate, method for producing metal plate, and method for producing vapor deposition mask using metal plate |
| JP5641462B1 (en) | 2014-05-13 | 2014-12-17 | 大日本印刷株式会社 | Metal plate, metal plate manufacturing method, and mask manufacturing method using metal plate |
| CN106460150B (en) | 2015-02-10 | 2020-01-10 | 大日本印刷株式会社 | Method for manufacturing vapor deposition mask, metal plate for manufacturing vapor deposition mask, and method for manufacturing metal plate |
| MX2018013741A (en) * | 2016-05-11 | 2019-08-16 | Nucor Corp | Cross-strip temperature variation control. |
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| AT357587B (en) * | 1976-02-18 | 1980-07-25 | Voest Alpine Ag | METHOD FOR PRODUCING SHEETS FROM AUSTENITIC STEELS WITH FINE GRAIN |
| JPS5913281B2 (en) * | 1978-09-25 | 1984-03-28 | 新日本製鐵株式会社 | Hot rolling method for metal slabs |
| JPS6044104A (en) * | 1983-08-22 | 1985-03-09 | Nippon Kokan Kk <Nkk> | Method for temper rolling |
| JPS6152317A (en) * | 1984-08-20 | 1986-03-15 | Kobe Steel Ltd | Manufacture of hot rolled steel plate having superior toughness at low temperature |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102154537A (en) * | 2011-02-14 | 2011-08-17 | 南京润邦金属复合材料有限公司 | Composite carbon tool steel/plain carbon steel metallurgical lining board with high resistance, high uniformity and long service life |
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| KR20050100701A (en) | 2005-10-19 |
| US20070051439A1 (en) | 2007-03-08 |
| JP2006520692A (en) | 2006-09-14 |
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| ATE366149T1 (en) | 2007-07-15 |
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| PT1599299E (en) | 2007-09-11 |
| MXPA05008979A (en) | 2006-04-27 |
| ZA200506720B (en) | 2006-11-29 |
| WO2004073900A1 (en) | 2004-09-02 |
| UA85550C2 (en) | 2009-02-10 |
| BRPI0407621A (en) | 2006-02-21 |
| AU2004213135A1 (en) | 2004-09-02 |
| EP1449596A1 (en) | 2004-08-25 |
| EP1599299B1 (en) | 2007-07-04 |
| RU2005129721A (en) | 2006-04-27 |
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