CN107739998B - A kind of preparation method of flat cold-rolled sheet - Google Patents
A kind of preparation method of flat cold-rolled sheet Download PDFInfo
- Publication number
- CN107739998B CN107739998B CN201710958307.6A CN201710958307A CN107739998B CN 107739998 B CN107739998 B CN 107739998B CN 201710958307 A CN201710958307 A CN 201710958307A CN 107739998 B CN107739998 B CN 107739998B
- Authority
- CN
- China
- Prior art keywords
- rolling
- temperature
- cold
- heating
- rolled sheet
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
- C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous 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
- C21D8/02—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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
- C22C38/12—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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
-
- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Abstract
The present invention relates to a kind of preparation method of flat cold-rolled sheet, the low expansion superalloy flat cold-rolled sheet without Cr, Al can be produced, the especially surface of GH2909 high temperature alloy, size, performance etc. is controlled, and the GH2909 alloy flat cold-rolled sheet of ingredient qualification is produced.This method include by manufactured steel billet successively after hot rolling, once cold rolling, primary annealing, secondary cold-rolling, double annealing to obtain the final product；Wherein, the condition once annealed are as follows: heating temperature: 970 ± 10 DEG C；Heating time is calculated by 1.5min/mm+3~5min, air-cooled；The condition of the double annealing are as follows: heating temperature: 960 ± 10 DEG C；Heating time is calculated by 1.5min/mm+3~5min, air-cooled.This method can have outstanding low expansion and mechanical property under the premise of keeping (≤the 0.6mm) of very thin thickness.
Description
Technical field
The present invention relates to metal material processing technical fields, in particular to a kind of preparation method of flat cold-rolled sheet.
Background technique
The development relationship of steel and iron industry the whole economic level of a national overall national strength and country, be national economy
One of basic industry in construction.Steel material is in the industries such as national defense industry, mechanical industry, building, automobile, shipbuilding and household electrical appliances
There is important application, is raw material indispensable in national manufacturing industry.In recent years, China has upgraded its industrial structure, is
The development of steel industry provides the space for continuing development, and the development of the national economy needs more and more high-quality steel products.
Cold-rolled thin sheet is the base stock for producing many important equipments, is occupied an important position in steel and iron industry production.
The production method of cold rolling can make the thinner of strip, moreover it is possible to improve the precision of rolling.The straightness of flat cold-rolled sheet is very high, tool
The bright surface of standby cleaning, is easy to carry out coating processing, punching performance with higher, not timeliness and yield point is very low, because
This flat cold-rolled sheet is received and is widely applied in automobile, building, bicycle, building materials, the printing industries such as metal bucket and coating steel plate.It is cold
Roll thin plate and be increasingly becoming the indispensable raw produce of some industries, in turn, relevant industries it is booming also promote it is cold
Roll the production of thin plate, simultaneously because lightweight, high-strength products concept it is universal, market is continuous to the quality requirement of flat cold-rolled sheet
It improves.
Currently, the production technology of cold-rolled thin sheet is more complicated, process is more, and quality is highly susceptible to influence.By
Raw material of the strip of hot rolling as production cold-reduced sheet, will be deformed by cold rolling, finally carry out the high temperature anneal simultaneously to it
Carry out finishing.Every procedure may all change the surface quality of sheet band, increase the difficulty that analysis causes product defects reason.
In the prior art, the coefficient of expansion of flat cold-rolled sheet is ideal not enough, and which has limited its uses in low bulk structural member.
In view of this, the present invention is specifically proposed.
Summary of the invention
The purpose of the present invention is to provide a kind of preparation methods of flat cold-rolled sheet, high to produce the low bulk without Cr, Al
Temperature alloy flat cold-rolled sheet.
In order to realize above-mentioned purpose of the invention, the following technical scheme is adopted:
The present invention relates to a kind of preparation methods of flat cold-rolled sheet comprising will plant chemical component mass percent are as follows: and C≤
0.06, Ni is 35.0~40.0, Co is 12.0~16.0, Nb is 4.3~5.2, Ti is 1.3~1.8, Si is 0.25~0.50, B
≤ 0.012, Mo≤0.20, Mn≤1.00, Al≤0.20, Cr≤1.00, Cu≤0.50, S≤0.015, P≤0.015, surplus are
Steel billet made of the steel grade of Fe successively after hot rolling, once cold rolling, primary annealing, secondary cold-rolling, double annealing to obtain the final product；
Wherein, the condition once annealed are as follows: heating temperature: 970 ± 10 DEG C；Heating time by 1.5min/mm+3~
5min is calculated, air-cooled；
The condition of the double annealing are as follows: heating temperature: 960 ± 10 DEG C；Heating time is based on 1.5min/mm+3~5min
It calculates, it is air-cooled.
By adjusting, optimization and flat cold-rolled sheet preparation process is improved, the present invention keeps a kind of low expansion superalloy cold rolling thin
The surface of plate, size, performance meet standard and user usage requirements, and it is thin to produce a kind of qualified low expansion superalloy cold rolling
Panel products improve product quality, create more economic benefits for enterprise.Compared with prior art, the present invention is being kept very
There is outstanding low expansion and mechanical property under the premise of (≤the 0.6mm) of thin thickness.
Detailed description of the invention
It, below will be to specific in order to illustrate more clearly of the specific embodiment of the invention or technical solution in the prior art
Embodiment or attached drawing needed to be used in the description of the prior art be briefly described, it should be apparent that, it is described below
Attached drawing is some embodiments of the present invention, for those of ordinary skill in the art, before not making the creative labor
It puts, is also possible to obtain other drawings based on these drawings.
Fig. 1 is 6 tons of induction furnace melting power curve of GH2909 alloy；
Fig. 2 is steel ingot Homogenization Treatments and forging technology curve；
Fig. 3 is blank heating curve among forging finished product.
Specific embodiment
The present invention relates to a kind of preparation methods of flat cold-rolled sheet comprising will plant chemical component mass percent are as follows: and C≤
0.06, Ni is 35.0~40.0, Co is 12.0~16.0, Nb is 4.3~5.2, Ti is 1.3~1.8, Si is 0.25~0.50, B
≤ 0.012, Mo≤0.20, Mn≤1.00, Al≤0.20, Cr≤1.00, Cu≤0.50, S≤0.015, P≤0.015, surplus are
Steel billet made of the steel grade of Fe successively after hot rolling, once cold rolling, primary annealing, secondary cold-rolling, double annealing to obtain the final product；
Wherein, the condition once annealed are as follows: heating temperature: 970 ± 10 DEG C；Heating time by 1.5min/mm+3~
5min is calculated, air-cooled；
The condition of the double annealing are as follows: heating temperature: 960 ± 10 DEG C；Heating time is based on 1.5min/mm+3~5min
It calculates, it is air-cooled.
Preferably, the preparation method of flat cold-rolled sheet as described above, the once cold rolling control cold rolling total deformation exist
30%~35%；The secondary cold-rolling control cold rolling total deformation is 30~35%.
Preferably, the preparation method of flat cold-rolled sheet as described above, the parameter of the hot rolling are as follows:
Famine rolls 1000 ± 10 DEG C of temperature, and 970 ± 10 DEG C of final rolling temperature, famine rolls 800 DEG C of finishing temperature >, finish rolling finishing temperature
800 DEG C of >；Heating time is calculated by 1.5min/mm+3-5min.Maximum pass deformation < 25%, last time deflection 20
~25%.
Preferably, the preparation method of flat cold-rolled sheet as described above is further including that soda acid is washed and white after double annealing
Change step.
Preferably, the preparation method of flat cold-rolled sheet as described above, the steel billet are melted by the steel grade by vacuum induction
Refining and vacuum consumable refusion and smelting process route obtain steel ingot, will obtain steel billet after the steel ingot hammer cogging, rolling-cogging.
Preferably, the preparation method of flat cold-rolled sheet as described above, the hammer cogging include:
Single arm or the fire forging of quick forging machine or precise forging machine end: 980 DEG C~1020 DEG C of heating temperature, deformation temperature control exists
955 DEG C~980 DEG C, deflection >=40%；
It is furthermore preferred that heating temperature is 990 DEG C~1010 DEG C, deformation temperature control at 960 DEG C~975 DEG C, deflection >=
43%.
Preferably, the preparation method of flat cold-rolled sheet as described above, the rolling-cogging include:
Slab rolling is carried out after blank after hammer cogging is heated cogging in the continuous oven of milling train.
Preferably, the preparation method of flat cold-rolled sheet as described above, the condition of the heating cogging are as follows:
Charging temperature≤700 DEG C, 1110 ± 10 DEG C of heating temperature, heating time >=4h, soaking time 2h.
Preferably, the preparation method of flat cold-rolled sheet as described above, the slab rolling include: by slab through one fire of milling train
Multi-pass rolls into the slab of required size, stops rolling temperature >=950 DEG C, passage maximum deformation quantity≤25%.
Preferably, the preparation method of flat cold-rolled sheet as described above, the chemical component mass percent of the steel grade are as follows: C
≤ 0.012, Ni is 37.8~38.8, Co is 12.8~13.8, Nb is 4.6~5.0, Ti is 1.4~1.7, Si be 0.35~
0.47, B≤0.01, Mo≤0.20, Mn < 0.5, Al < 0.06, Cr < 0.2, Cu < 0.1, S≤0.015, P≤0.015；
It is furthermore preferred that the preparation method of flat cold-rolled sheet as described above, the chemical component mass percent of the steel grade are as follows:
C≤0.012, Ni are 38.2~38.7, Co is 12.8~13.8, Nb is 4.6~5.0, Ti is 1.4~1.7, Si be 0.35~
0.47, B≤0.01, Mo≤0.20, Mn < 0.5, Al < 0.06, Cr < 0.2, Cu < 0.1, S≤0.015, P≤0.015.
Embodiment of the present invention is described in detail below in conjunction with embodiment, but those skilled in the art will
Understand, the following example is merely to illustrate the present invention, and is not construed as limiting the scope of the invention.It is not specified in embodiment specific
Condition person carries out according to conventional conditions or manufacturer's recommended conditions.Reagents or instruments used without specified manufacturer is
It can be with conventional products that are commercially available.
Embodiment
1 scope of application
GH909 alloy is a kind of Fe-Ni-Co base age-hardening type low bulk to grow up on the basis of GH907 alloy
High temperature alloy, compared with GH907 alloy, the stress of alloy promotes grain boundary oxidation brittleness (SAGBO) drag and creep rupture life to obtain
It further increases, but thermal expansion coefficient and GH903, GH907 are essentially identical, performance can meet the following turbine hair of three generations substantially
The demand of motivation, it has low thermal expansion coefficient, nearly constant elasticity modulus and good comprehensive mechanical property, answers extensively
For the clearance component between rotatable parts and stationary parts, gap control technology is realized, it is energy saving, consumption is reduced, is improved
Motor power, but since alloy is free of Cr, the disadvantage is that oxidation drag and corrosion resistance are very low, especially anti-oxidant problem,
650 DEG C or more GH909 alloys cannot completely it is anti-oxidant.
GH2909 alloy melting point is about 1336~1384 DEG C, and specific gravity is about 8.26g/cm3。
2 technical conditions
Q/S15.2206-2011 etc.
3 process routes
Vacuum induction+vacuum consumable
4 technical requirements
4.1 vacuum induction melting techniques
4.1.1 6 tons of vacuum induction melting technique
4.1.1.1 equipment requirement:
Wind, water, electricity, vacuum system and each mechanical equipment work well.
4.1.1.2 melting condition:
New crucible smelting needs Fe to wash 2 furnaces, and the second furnace iron washes that (pure 00), centre, which smelts, needs iron to wash (pure 00), 1 furnace with smart steel.
4.1.1.3 raw material
Furnace charge by this steel return (≤50%), smart steel (CT1-1), 1#Ni, J-Co, monocrystalline silicon, graphite electrode, J-Nb,
Sponge Ti and Fe-B composition.Alloy material by raw material incoming inspection regulation into must carry out an acceptance inspection after factory, the surface of raw material, ruler
Very little, lumpiness requires to meet 6 tons of vaccum sensitive stove Elementary Procedures.
4.1.1.4 charge weight and electrode specification
Charge weight: 3200kg or 6400kg；Electrode:Zhi HuoBranch.
4.1.1.5GH2909 alloy composition is shown in Table 1.
GH2909 alloy composition ▲ (wt%) table 1
4.1.1.6 charging
4.1.1.6.1 forehearth Fe, which is washed, guarantees that CT1-1 wholeization is complete, and turns over net molten steel, avoids removing material in furnace.
4.1.1.6.2 it is all enter furnace raw material through direct labor, specific responsibility inspection personnel by charger sheet inspection, weighing, confirmation
Kind, quantity it is errorless and sign after can enter furnace.
4.1.1.6.3Ni, Co and smart steel (CT1-1) are once packed into crucible.C, Ti, Nb, Fe-B, Si are bent by smelting process
Line is added.
4.1.1.7 smelting process curve, such as Fig. 1.
4.1.1.8 smelting main points:
Refining temperature requires precise control, guarantees de- N effect, diligent to survey gentle agitation.Add ten minutes sampling analyses after Ti, adds
Reinforce stirring when material and sampling, controls tapping temperature.
4.1.1.9 casting
4.1.1.9.1 it is poured and carries out under vacuum, control poring rate and filling quality.
4.1.1.9.2 ingot mould must be scalded with molten steel, be cleaned rustless.
4.1.1.9.3 it is more than hour must to heat 4 for pans, and surface temperature must reach 1000 DEG C.
4.1.1.9.4 furnace cool time, which is greater than the side 1.5h, after being poured can break sky, take off ingot after the cold 2h of mould.
4.2 vacuum consumable remeltings
4.2.1 melting condition
Equipment must be checked before melting, confirmation equipment is good, vacuum degree of cold state < 0.67Pa, gas leakage degree <
The side 0.67Pa/min can smelt.
4.2.2 consutrode
It cuts end to end only, surface must be clean through abrasion wheel grinding, if shrinkage cavity is towards lower from expendable weight after the bad cleaning that need to strip off the skin in surface
It is molten.
4.2.3 consumable technique
4.2.3.1 the side 0.67Pa vacuum degree < can be to the electric starting the arc.
4.2.3.2 crystallizer:
4.2.3.3 electric power system
Ingot, electric current 7000A or so, 22~24V of voltage or so.
Electric current is subject to molten bath to the minimum current on side.Melting is carried out by electrical force profiles.
It carries out rushing helium gas cooling, pressure 600Pa in reflow process.
4.2.3.4 certain it is noted that filling quality, gradually decreases electric current.Each stage keeps certain time, can not be once
Low current is dropped to, shrinks molten bath as far as possible, is mentioned in shrinkage cavity, lumber recovery is improved.
4.2.4 filling process: starting to fill in electrode 200 ± 10kg of residue, and filling is with reference to technique and steps are as follows:
| Step | Electric current (A) | Voltage (V) | Retention time (min) |
| 1 | 6000 | 23 | 3 |
| 2 | 5500 | 22.8 | 5 |
| 3 | 4500 | 22.6 | 8 |
| 4 | 4000 | 22.5 | 10 |
| 5 | 3500 | 22.0 | 5-10 |
| 6 | 2000 | 21.7 | 5-10 |
| 7 | 2000 | 20.0 | 5-10 |
4.3. Homogenization Treatments
Homogenization Treatments are carried out to steel ingot.Pay attention to steel ingot strict temperature control in Homogenization Treatments, there can be no temperature
Fluctuate the warm phenomenon of excessive and race.Homogenization Treatments system is shown in that Fig. 2, steel ingot are heated in bell furnace.
4.4. forging technology
4.4.1 steel ingot cogging forging is forged fastly in 2000t or 4500t carries out.
4.4.2 heating cycle
Heating cycle curve, such as Fig. 2:
4.4.3 forging technology
Cogging forging: generalling use multiple upsetting pull technique, and specific deformation scheme view trimmed size determines；
4.4.3.1 finish forge unit heating process
The following are intermediate base heating curves, when production, can be according to intermediate base size appropriate adjustment soaking time, with blank temperature
Degree uniformly arrives subject to temperature.
Forging is become a useful person: Single arm or the fire forging of quick forging machine or precise forging machine end: 980~1020 DEG C of heating temperature, being seen Fig. 3, is become
Shape temperature is controlled at 955~980 DEG C, and deflection >=40% can not melt down empty burning.
4.4.4 for rolling blank, cogging can be carried out in Single arm.
4.5. rolling mill practice
4.5.1 heating cycle
Blank heats in the continuous oven of milling train.Charging temperature≤700 DEG C, 1110 ± 10 DEG C of heating temperature, heating time
>=4h, soaking time 2h.
4.5.2 slab rolling
Slab rolls into the slab of required size through the fiery multi-pass of milling train one, stops rolling temperature >=950 DEG C, passage maximum deformation quantity
≤ 25%.It flows down after blank surface whole peeling, and takes low power end to end as required.
4.5.3 billet rolling
Square billet rolls into the bar or blank of required size through the fiery multi-pass of milling train one.
4.6. thin plate technique
4.6.1 hot rolling
Famine rolls 1000 ± 10 DEG C of temperature, and 970 ± 10 DEG C of final rolling temperature, famine rolls 800 DEG C of finishing temperature >, finish rolling finishing temperature
800 DEG C of >.Heating time is calculated by 1.5min/mm+3-5min.Maximum pass deformation < 25%, last time deflection 20
~25%.
4.6.2 cold rolling
Semi-finished product total deformation 30~35%, finished product total deformation 25~30%.
4.6.3 annealing
Annealing carries out in the furnace of roller bottom.
4.6.3.1 semi-finished product
Heating temperature: 970 ± 10 DEG C.
Heating time is calculated by 1.5min/mm+3~5min, air-cooled.
4.6.3.2 finished product
960 ± 10 DEG C of heating temperature.940 ± 10 DEG C of finished products temperature.
Heating time is calculated by 1.5min/mm+3~5min, air-cooled.
4.6.4 soda acid wash, albefaction
It is executed by iron-base superalloy technique.
4.6.5 finishing, inspection, flaw detection, packaging, storage.
4.7. unaccomplished matter is executed by basic operation regulation.
Experimental example
According to cold prepared by the GB/T 4339-2008 metal material thermal expansion character measurement method of parameters detection present invention
Roll the room temperature~600 DEG C average linear expansion coefficient of thin plate.Size of sample isDetection is (moral) using equipment
NETZSCH DIL 203SE dilatometer.Testing result is as shown in the table:
0.6mm thickness cold rolled sheet end properties are detected simultaneously, as a result as shown in the table:
Finally, it should be noted that the above embodiments are only used to illustrate the technical solution of the present invention., rather than its limitations；To the greatest extent
Present invention has been described in detail with reference to the aforementioned embodiments for pipe, but those skilled in the art should understand that: its
It is still possible to modify the technical solutions described in the foregoing embodiments, or to some or all of the technical features
It is equivalently replaced；And these are modified or replaceed, various embodiments of the present invention skill that it does not separate the essence of the corresponding technical solution
The range of art scheme.
Claims (2)
1. a kind of preparation method of flat cold-rolled sheet comprising by chemical component mass percent are as follows: C≤0.012, Ni be 37.8~
38.8, Co is 12.8~13.8, Nb is 4.6~5.0, Ti is 1.4~1.7, Si is 0.35~0.47, B≤0.01, Mo≤
0.20, Mn < 0.5, Al < 0.06, Cr < 0.2, Cu < 0.1, S≤0.015, P≤0.015, surplus are made of the steel grade of Fe
Steel billet successively after hot rolling, once cold rolling, primary annealing, secondary cold-rolling, double annealing to obtain the final product；The steel billet is by the steel grade
Steel ingot is obtained by vacuum induction melting and vacuum consumable refusion and smelting process route, the steel ingot hammer cogging, rolling are opened
Steel billet is obtained after base；
The hammer cogging includes:
Single arm or the fire forging of quick forging machine or precise forging machine end: 980 DEG C~1020 DEG C of heating temperature, deformation temperature is controlled at 955 DEG C
~980 DEG C, deflection >=40%；
The rolling-cogging includes:
Slab rolling is carried out after blank after hammer cogging is heated cogging in the continuous oven of milling train；
The condition of the heating cogging are as follows:
Charging temperature≤700 DEG C, 1110 ± 10 DEG C of heating temperature, heating time >=4h, soaking time 2h；
The slab rolling includes: the slab that slab is rolled into required size through the fiery multi-pass of milling train one, stops rolling temperature >=950
DEG C, passage maximum deformation quantity≤25%；
The parameter of the hot rolling are as follows:
Famine rolls 1000 ± 10 DEG C of temperature, and 970 ± 10 DEG C of final rolling temperature, famine rolls 800 DEG C of finishing temperature >, finish rolling finishing temperature >
800℃；Heating time is calculated by 1.5min/mm+3-5min；Maximum pass deformation < 25%, last time deflection 20~
25%；
The once cold rolling control cold rolling total deformation is 30%~35%；The secondary cold-rolling control cold rolling total deformation is 30
~35%；
Wherein, the condition once annealed are as follows: heating temperature: 970 ± 10 DEG C；Heating time presses 1.5min/mm+3~5min
It calculates, it is air-cooled；
The condition of the double annealing are as follows: heating temperature: 960 ± 10 DEG C；Heating time is calculated by 1.5min/mm+3~5min,
It is air-cooled.
2. the preparation method of flat cold-rolled sheet according to claim 1, which is characterized in that further including after double annealing
Soda acid is washed and albefaction step.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710958307.6A CN107739998B (en) | 2017-10-16 | 2017-10-16 | A kind of preparation method of flat cold-rolled sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710958307.6A CN107739998B (en) | 2017-10-16 | 2017-10-16 | A kind of preparation method of flat cold-rolled sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107739998A CN107739998A (en) | 2018-02-27 |
| CN107739998B true CN107739998B (en) | 2019-06-21 |
Family
ID=61237587
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710958307.6A Active CN107739998B (en) | 2017-10-16 | 2017-10-16 | A kind of preparation method of flat cold-rolled sheet |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN107739998B (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109136717A (en) * | 2018-11-07 | 2019-01-04 | 成都先进金属材料产业技术研究院有限公司 | Low expansion superalloy heat treatment method |
| CN110527892A (en) * | 2019-10-10 | 2019-12-03 | 成都先进金属材料产业技术研究院有限公司 | Low expansion superalloy and preparation method thereof |
| CN114045436A (en) * | 2021-11-12 | 2022-02-15 | 成都先进金属材料产业技术研究院股份有限公司 | GH2909 alloy ingot and preparation method thereof |
| CN115161444B (en) * | 2022-08-12 | 2024-01-19 | 山西太钢不锈钢精密带钢有限公司 | Low-expansion alloy 4J36 precise foil and superfine crystal solid solution heat treatment method and application thereof |
| CN117363960B (en) * | 2023-12-08 | 2024-03-08 | 成都先进金属材料产业技术研究院股份有限公司 | Low-carbon aluminum-free high-niobium-iron-based superalloy and preparation method thereof |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5211772A (en) * | 1990-12-28 | 1993-05-18 | Kabushiki Kaisha Kobe Seiko Sho | Wire rod for high strength and high toughness fine steel wire, high strength and high toughness fine steel wire, twisted products using the fine steel wires, and manufacture of the fine steel wire |
| JPH06172926A (en) * | 1992-12-09 | 1994-06-21 | Hitachi Metals Ltd | Roll for rolling glass |
| CN1100160C (en) * | 2000-12-12 | 2003-01-29 | 钢铁研究总院 | High-strength alloy with constant elasticity at high temp and its preparing process |
| DE10258356B3 (en) * | 2002-12-12 | 2004-05-27 | Thyssenkrupp Vdm Gmbh | Use of an iron-nickel-cobalt alloy for shadow masks and their frames in flat monitors and TV screens |
| JP4908137B2 (en) * | 2006-10-04 | 2012-04-04 | 株式会社東芝 | Turbine rotor and steam turbine |
| CN104328325B (en) * | 2014-09-29 | 2017-05-17 | 钢铁研究总院 | Iron-nickel-based low-delaying constant-elastic alloy used in diaphragm capsule sensor and preparation method thereof |
-
2017
- 2017-10-16 CN CN201710958307.6A patent/CN107739998B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN107739998A (en) | 2018-02-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107739998B (en) | A kind of preparation method of flat cold-rolled sheet | |
| CN108179322B (en) | A kind of preparation method of the difficult deformation cobalt base superalloy plate of high lanthanum content | |
| CN103949805B (en) | A kind of method preparing nickel-base alloy bare welding filler metal | |
| CN106734805B (en) | Φ 500~650mm Cr6 swaged forging Electro Slag Remelting Steel cold roll blank forging deformation techniques | |
| CN102230120B (en) | High-performance elastic alloy material for aerial hyperbaric cabin and production method thereof | |
| CN100494459C (en) | Electric resistance alloy and its preparing process | |
| CN106282836A (en) | Steam turbine is by 2Cr11MoVNbN forging and manufacture method thereof | |
| CN103949806B (en) | A kind of preparation method of welding wire | |
| CN103949798B (en) | A kind of preparation method of nickel-base alloy bare welding filler metal | |
| CN105839028B (en) | Austenite heat-resistance Valve Steel manufacture method | |
| CN101748314A (en) | Nickel-based alloy of nuclear power steam generator | |
| CN104805352A (en) | Production method of cold-rolled steel plate for electro-galvanization | |
| CN108672625A (en) | A kind of processing method producing multi-step cold roll base using diameter forging machine | |
| CN109266881A (en) | A kind of preparation process of 5083 aluminium alloy of high buckling performance | |
| CN110230005B (en) | Steel for high-carbon chromium cold roll blank and preparation method thereof | |
| CN102000954A (en) | Method for manufacturing continuous pipe mill retained mandrel | |
| CN104789864A (en) | Hot-rolled steel strip used for enamel and having ultra-deep-punching performance and preparation method of hot-rolled steel strip | |
| CN109468561A (en) | A kind of preparation method of GH3625 alloy strip steel rolled stock | |
| CN112143975A (en) | Economical high-efficiency X70-grade pipeline steel and manufacturing method thereof | |
| CN109518079A (en) | A kind of production method of hydrogen-contacting equipment 15CrMoR steel plate | |
| CN102059271B (en) | Manufacture method of seamless steel tube for (ultra-)supercritical boiler | |
| CN105108377A (en) | Nickel alloy welding wire for welding cast iron pipe | |
| CN105624565A (en) | Chrome-plating-free cold roll and producing method thereof | |
| CN105839021A (en) | Rare-earth-containing high-chromium-content ferritic stainless steel and manufacturing method of steel pipe therefrom | |
| CN110284054A (en) | A kind of high temperature resistant resistance to deformation electrolytic cell steel and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |