CN112301272B - High-yield steel for one-time cold rolling cover unpacking and preparation method thereof - Google Patents
High-yield steel for one-time cold rolling cover unpacking and preparation method thereof Download PDFInfo
- Publication number
- CN112301272B CN112301272B CN202011044915.4A CN202011044915A CN112301272B CN 112301272 B CN112301272 B CN 112301272B CN 202011044915 A CN202011044915 A CN 202011044915A CN 112301272 B CN112301272 B CN 112301272B
- Authority
- CN
- China
- Prior art keywords
- rolling
- steel
- controlled
- cold
- yield
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention particularly relates to high-yield steel for one-time cold rolling cover unpacking and a preparation method thereof, belonging to the technical field of steel preparation, wherein the high-yield steel for one-time cold rolling cover unpacking comprises the following chemical components in percentage by mass: c: 0.050-0.075%, Si not more than 0.02%, Mn: 0.20-0.40%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.006-0.015%, N: 0.0160-0.0190% and the balance of Fe and inevitable impurities; by increasing N and reducing Als, the precipitation of AIN is inhibited, N element added in the steel is mainly stored in the steel in a solid solution mode, and the strengthening effect of C, Mn is matched, so that the strength and the yield property of the steel for packaging are improved, and the alloy cost is reduced.
Description
Technical Field
The invention belongs to the technical field of steel preparation, and particularly relates to high-yield steel for one-time cold rolling cover unpacking and a preparation method thereof.
Background
The steel for once cold rolling cover annealing packaging is a cold rolling cover annealing low carbon steel plate or steel strip which is obtained by electroplating operation and is coated with a tin layer or a chromium layer on two surfaces, and is mainly used for the fields of beverage cans, food cans, spray cans, chemical industry cans and the like.
Currently, European Standard EN 10202-2001-Cold reduced thin products-Electrolytic coating and Electrolytic chromium/chromium oxide coated Steel-the highest yield strength grade of steel for primary Cold-rolling mask unpacking is 290 MPa. The highest yield strength level of the steel for one-time Cold-rolling cover unpacking in ISO 11949-2016 Cold-reduced and rolling products-electric rolling plate and ISO 11950-2016-Cold-reduced and rolling products-electric rolling/rolling oxide-coated steel is 340 MPa. The steel for once cold rolling cover depacking with the strength grade of more than 340MPa is rarely reported.
Corresponding researches are also carried out on the cover deplating tin plate in China, for example, in a patent CN200910063099.9, the components of 0.08-0.13 percent of C, less than or equal to 0.025 percent of Si, 0.47-0.65 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.020 percent of S, 0.02-0.06 percent of Als, less than or equal to 0.005 percent of N and 0.01-0.03 percent of Ti are adopted, the performance is improved by adding C, Mn and Ti, and the cost is high; the patent CN201510125544.5 adopts the components of C0.01%, Si 0.02%, Mn0.10%, P0.009%, S0.012%, Als0.005%, N0.0025%, Sn0.011% and As0.006% to produce only T-1TS230 low-strength tin plate. Meanwhile, the yield ratio of the packaging steel is generally 0.88 or more as the strength is increased. Therefore, how to produce the steel for the once cold rolling cage depacking with high strength and low yield ratio at low cost is a great problem.
Disclosure of Invention
In view of the above problems, the present invention has been made in order to provide a high yield steel for one-time cold rolled cap rejection packaging and a method for manufacturing the same, which overcomes or at least partially solves the above problems.
The embodiment of the invention provides high-yield steel for one-time cold rolling cover depacketizing, which comprises the following chemical components in percentage by mass: c: 0.045-0.08%, Si is less than or equal to 0.02%, Mn: 0.15-0.45%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.005-0.018%, N: 0.0150-0.020%, and the balance of Fe and inevitable impurities.
Optionally, the steel comprises the following chemical components in percentage by mass: c: 0.050-0.075%, Si not more than 0.02%, Mn: 0.20-0.40%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.006-0.015%, N: 0.0160-0.0190% and the balance of Fe and inevitable impurities.
Optionally, the metallographic structure of the steel is, in terms of volume fraction: 97-99% of ferrite and 1-3% of cementite.
Optionally, the ferrite grain size is 4.0-6.0 μm.
Based on the same inventive concept, the embodiment of the invention also provides a preparation method of the high-yield steel for the one-time cold-rolled cap depacketizing, which comprises the following steps:
obtaining a casting blank of the high-yield one-time cold-rolled cover unpacking steel;
sequentially carrying out hot rolling, pickling, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover annealing packaging,
the hot rolling procedure comprises the steps of heating a casting blank, rough rolling, finish rolling and coiling, wherein the heating temperature of the casting blank is 1180-,
the annealing temperature of the cover annealing is 610-640 ℃,
the flat elongation is 1.0-2.5%.
Optionally, in the step of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be less than or equal to 20 ℃, and the heating time is controlled to be 2.5-4.0 h.
Optionally, in the rough rolling, rolling is performed by 5-8 passes, and the total deformation of the rough rolling is controlled to be 83-86%.
Optionally, in the precision rolling, 7 passes of rolling are adopted, the rolling speed is controlled to be 10-16m/s, the total deformation amount of the precision rolling is controlled to be 92-95%, and the outlet temperature of the precision rolling is 850-.
Optionally, in the cold rolling, the cold rolling reduction is controlled to be 80-92%, and the thickness of the cold rolled plate obtained by the cold rolling is controlled to be 0.17-0.50 mm.
Optionally, in the hood annealing, the heat preservation time is controlled to be 10-14 h.
One or more technical solutions in the embodiments of the present invention have at least the following technical effects or advantages:
the steel for the once-through cold rolling cover depacking and packaging with high yield provided by the embodiment of the invention comprises the following chemical components in percentage by mass: c: 0.050-0.075%, Si not more than 0.02%, Mn: 0.20-0.40%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.006-0.015%, N: 0.0160-0.0190% and the balance of Fe and inevitable impurities; by increasing N and decreasing Als, AlN precipitation is suppressed, N element added to the steel is mainly contained in the steel in a solid solution manner, and C, Mn is added to enhance the strength and yield property of the steel for packaging, and alloy cost is reduced.
The foregoing description is only an overview of the technical solutions of the present invention, and the embodiments of the present invention are described below in order to make the technical means of the present invention more clearly understood and to make the above and other objects, features, and advantages of the present invention more clearly understandable.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments and examples, and the advantages and various effects of the present invention will be more clearly apparent therefrom. It will be understood by those skilled in the art that these specific embodiments and examples are for the purpose of illustrating the invention and are not to be construed as limiting the invention.
Throughout the specification, unless otherwise specifically noted, terms used herein should be understood as having meanings as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. If there is a conflict, the present specification will control.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
In order to solve the technical problems, the general idea of the embodiment of the application is as follows:
according to an exemplary embodiment of the invention, the steel for the once-through cold rolling cage depacketizing with high yield comprises the following chemical components in percentage by mass: c: 0.045-0.08%, Si is less than or equal to 0.02%, Mn: 0.15-0.45%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.005-0.018%, N: 0.0150-0.020%, and the balance of Fe and inevitable impurities.
C is used as a solid solution strengthening element, the mass fraction of C is controlled to be 0.050-0.075% so as to ensure good strong plasticity and production stability, excessive mass fraction value can cause chemical components to enter a peritectic zone, slab cracks can be easily caused, plasticity can be reduced, and excessive mass fraction value can cause steel strength reduction, and meanwhile, the increase of phase transition temperature can easily cause mixed crystals at the edge of a hot rolled plate to influence performance uniformity;
si is used as a solid solution strengthening element, the mass fraction of Si is controlled to be less than or equal to 0.02% so as to improve the surface quality, the excessive mass fraction can cause the easy occurrence of iron scale defects and the deterioration of the surface quality, and the excessive mass fraction can cause the increase of the production cost;
mn is used as a solid solution strengthening element, the mass fraction of Mn is controlled to be 0.20-0.40% so as to ensure the performance of a finished product, the smelting cost is controlled, and the excessively large mass fraction can cause the improvement of the smelting cost, and the excessively small mass fraction can cause the reduction of the performance of the finished product;
the effect of P is to deteriorate plasticity, the quality fraction of P is controlled to be less than or equal to 0.015 percent so as to improve the plasticity and prevent cold brittleness, and the too large value of the quality fraction can cause the plasticity to be reduced, and the too small value can cause the production cost to be increased;
the S is used as an impurity element, the mass fraction of the S is controlled to be less than or equal to 0.012 percent so as to improve plasticity and reduce the generation of MnS inclusions, and the too large value of the mass fraction can cause the reduction of plasticity and the too small value can cause the increase of production cost;
the Alt is used for deoxidizing and fixing nitrogen elements, the mass fraction of the Alt is controlled to be 0.006-0.015% so as to remove oxygen in steel and reduce inclusions, excessive solid-solution N elements can be caused by excessively large mass fraction value, the N solid-solution strengthening effect is weakened, the performance of a finished product is reduced, insufficient deoxidation can be caused by excessively small mass fraction value, and more inclusions are generated;
n acts as a solid solution strengthening element to control the quality of N
The mass fraction of 0.0160-0.0190% is used for producing a solid solution strengthening effect, improving the performance of a finished product and reducing the content of Mn element, and the excessive mass fraction may cause slab defects and the insufficient mass fraction may not provide sufficient strengthening effect.
Optionally, the steel comprises the following chemical components in percentage by mass: c: 0.050-0.075%, Si not more than 0.02%, Mn: 0.20-0.40%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.006-0.015%, N: 0.0160-0.0190% and the balance of Fe and inevitable impurities.
Optionally, the metallographic structure of the steel is, in terms of volume fraction: 97-99% of ferrite and 1-3% of cementite.
The ferrite with the volume fraction of 97-99% has the function of ensuring plasticity, and the excessive volume fraction can cause the strength to be reduced, and the insufficient volume fraction can cause the plasticity to be reduced.
The effect of the cementite with the volume fraction of 1-3% is to produce the strengthening effect, and the too large volume fraction may cause the reduction of plasticity, and the too small volume fraction may cause the reduction of strength.
The ferrite provides plasticity, and the cementite provides strength and hardness, so that the plasticity, the strength and the hardness are matched.
Optionally, the ferrite grain size is 4.0-6.0 mm.
The effect that the grain size of ferrite is 4.0-6.0mm is to provide reasonable fine grain strengthening effect, the too large value of the grain size can weaken the fine grain strengthening effect and reduce the performance of the finished product, and the too small value can cause the too strong fine grain strengthening effect, improve the yield ratio and reduce the formability.
According to another exemplary embodiment of the present invention, the embodiment of the present invention further provides a method for preparing a high yield steel for one-time cold rolling cap unpacking, the method including:
s1, obtaining a casting blank of the high-yield primary cold-rolled cover unpacking steel;
s2, sequentially carrying out hot rolling, pickling, cold rolling, cover annealing and flattening on the casting blank to obtain the high-yield steel for the primary cold-rolled cover depacketizing, wherein the thickness of the high-yield steel for the primary cold-rolled cover depacketizing can be 0.17-0.50mm,
the hot rolling procedure comprises the steps of heating a casting blank, rough rolling, finish rolling and coiling, wherein the heating temperature of the casting blank is 1180-,
the annealing temperature of the cover annealing is 610-640 ℃,
the flat elongation is 1.0-2.5%.
The heating temperature is controlled to be 1180-1240 ℃, so that complete solid solution of N is ensured, the excessive temperature value may cause increase of oxidation burning loss, and the excessive temperature value may cause reduction of the solid solution amount of N; the coiling temperature is controlled to be 550-640 ℃ to ensure N solid solution and reduce N precipitation, and the excessive temperature value can cause the increase of N precipitation and the reduction of solid solution strengthening effect, and the excessive temperature value can cause the easy generation of plate shape defects; the N element in the plate blank is completely dissolved at a reasonable heating temperature, excessive oxidation is prevented, and then the N element is dissolved in the steel after coiling by adopting a low-temperature coiling process, so that the solid solution strengthening effect is provided, and precipitation is avoided;
ferrite grains are fully recrystallized after cover annealing, the yield ratio is reduced, the annealing temperature is controlled to be 610-640 ℃ so as to obtain reasonable grain size, coarsening grains can be caused by overlarge temperature value, the performance of a finished product is reduced, grains can be excessively refined and even incomplete recrystallization can be caused by undersize, and the plasticity is reduced;
the flattening elongation is controlled to be 1.0-2.5% so as to control the strength and the hardness, and the overlarge flattening elongation can cause overlarge rolling force, the large plate shape control difficulty and the undersize can cause lower strength and hardness.
Optionally, in the step of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be less than or equal to 20 ℃, and the heating time is controlled to be 2.5-4.0 h.
The temperature difference of the cross section of the casting blank is controlled to be less than or equal to 20 ℃ so as to ensure the performance uniformity, and the excessive temperature difference can cause the reduction of the uniformity of N solid solution and the performance uniformity;
the heating time is controlled to be 2.5-4.0h to ensure the uniform temperature of the plate blank and reduce the oxidation burning loss.
Optionally, in the rough rolling, rolling is performed by 5-8 passes, the rolling speed is controlled to be-mm/s, and the total deformation of the rough rolling is controlled to be 83-86.
The rough rolling is carried out by adopting 5-8 passes so as to roll to the required thickness of an intermediate billet in reasonable rolling passes and prepare for finish rolling;
the total deformation of the rough rolling is controlled to be 83-86% so as to lead the austenite to be statically recrystallized and refine grains during the rough rolling, and the excessive or insufficient value of the total deformation can cause the production difficulty to be increased and the austenite grains to be coarsened respectively.
Optionally, in the precision rolling, 7 passes of rolling are adopted, the rolling speed is controlled to be 10-16mm/s, the total deformation amount of the precision rolling is controlled to be 92-95%, and the outlet temperature of the precision rolling is 850-.
The finish rolling is carried out by adopting 7 times so as to fully refine the crystal grains by accumulating enough deformation;
the finish rolling speed is controlled to be 10-16mm/s so as to reduce the temperature drop of the edge part, improve the uniformity of the texture of the edge part and improve the production efficiency, and the overlarge or undersize value can cause the increase of the production difficulty and the reduction of the performance uniformity of a finished product respectively;
the total deformation of the finish rolling is controlled to be 92-95% so as to accumulate enough deformation to fully refine crystal grains, and the excessive or insufficient value can cause the increase of rolling load and coarsening of hot rolling crystal grains respectively;
the outlet temperature of the finish rolling is controlled to be 850-900 ℃ so as to ensure that the finish rolling is finished in an austenite region, mixed crystals are avoided, and excessive or insufficient values can cause the increase of iron scale defects and the reduction of the uniformity of the structure.
Optionally, in the cold rolling, 80-92% of the cold-rolled plate obtained by the cold rolling is controlled to have a thickness of 0.17-0.50 mm.
The cold rolling reduction rate is controlled to be 80-92% so as to break a hot rolling structure, increase recrystallization driving force, reduce annealing temperature and reduce annealing cost, and excessively large or excessively small values respectively can cause increase of cold rolling force and easy occurrence of strip breakage risk, or reduce recrystallization driving force, so that annealing temperature is increased and cost is increased.
Optionally, in the hood annealing, the heat preservation time is controlled to be 10-14 h.
The heat preservation time is controlled to be 10-14h so as to ensure that the annealing temperature of the whole coil is uniform and the coil passing performance is stable, and the excessively large value or excessively small value can cause the increase of the production cost and the reduction of the stability of the coil passing performance.
The steel for high yield one-pass cold rolled cage depacking and the method for manufacturing the same according to the present application will be described in detail with reference to examples, comparative examples and experimental data.
Example 1
The high-yield steel for once cold-rolled cap unpacking comprises the following chemical components in percentage by mass:
c: 0.073%, Si: 0.01%, Mn: 0.38%, P: 0.010%, S: 0.006%, Als: 0.014%. N: 0.0178%, and the balance of Fe and inevitable impurities.
The embodiment also provides a preparation method of the steel for the package removal of the high-yield one-time cold-rolled cover, which comprises the following steps:
s1, obtaining a casting blank of the high-yield primary cold-rolled cover unpacking steel;
s2, sequentially carrying out hot rolling, acid washing, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover-annealing packaging,
the hot rolling procedure comprises the steps of casting blank heating, rough rolling, finish rolling and coiling:
in the process of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be less than or equal to 19 ℃, the heating temperature of the casting blank is controlled to be 1198 ℃, and the heating time is controlled to be 3.0h.
In rough rolling, 1+5 passes of rolling are adopted, and the total deformation of the rough rolling is controlled to be 85%;
in the fine rolling, 7 passes are adopted for rolling, the rolling speed is controlled to be 15m/s, the total deformation of the fine rolling is controlled to be 94 percent, the outlet temperature of the fine rolling is 881 ℃,
the coiling temperature is 591 ℃;
in the cold rolling, the cold rolling reduction is controlled to be 89%, and the thickness of the cold-rolled plate obtained by the cold rolling is controlled to be 0.24 mm;
in the cover type annealing, the annealing temperature is controlled to be 619 ℃, and the heat preservation time is controlled to be 11.5 h;
the flat elongation was 2.5%.
In this example, the thickness of the high yield steel for one-time cold rolling cover unpacking is 0.24mm, and the metallographic structure of the steel is, in terms of volume fraction: 98% ferrite, 2% cementite, wherein the grain size of the ferrite is 5.2 mm.
Example 2
The high-yield steel for once cold-rolled cap unpacking comprises the following chemical components in percentage by mass:
c: 0.06%, Si: 0.015%, Mn: 0.31%, P: 0.009%, S: 0.007%, Als: 0.008%, N: 0.0165%, and the balance of Fe and inevitable impurities.
The embodiment also provides a preparation method of the steel for the package removal of the high-yield one-time cold-rolled cover, which comprises the following steps:
s1, obtaining a casting blank of the high-yield primary cold-rolled cover unpacking steel;
s2, sequentially carrying out hot rolling, acid washing, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover-annealing packaging,
the hot rolling procedure comprises the steps of casting blank heating, rough rolling, finish rolling and coiling:
in the process of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be less than or equal to 18 ℃, the heating temperature of the casting blank is controlled to be 1230 ℃, and the heating time is controlled to be 4 hours.
In rough rolling, 3+3 passes are adopted for rolling, and the total deformation of the rough rolling is controlled to be 86%;
in the fine rolling, 7-pass rolling is adopted, the rolling speed is controlled to be 15mm/s, the total deformation of the fine rolling is controlled to be 95%, the outlet temperature of the fine rolling is 877 ℃,
the coiling temperature is 585 ℃;
in the cold rolling, the cold rolling reduction is controlled to be 91 percent, and the thickness of the cold-rolled plate obtained by the cold rolling is controlled to be 0.18 mm;
in the cover annealing, the annealing temperature is controlled to be 632 ℃, and the heat preservation time is controlled to be 12.5 h;
the flat elongation is 2.2%;
in this example, the thickness of the high yield steel for one-time cold rolling cover unpacking is 0.18mm, and the metallographic structure of the steel is, in terms of volume fraction: 99% ferrite, 1% cementite, wherein the grain size of the ferrite is 5.8 mm.
Example 3
The high-yield steel for once cold-rolled cap unpacking comprises the following chemical components in percentage by mass:
c: 0.071%, Si: 0.008%, Mn: 0.36%, P: 0.013%, S: 0.009%, Als: 0.011%, N: 0.0181%, and the balance of Fe and inevitable impurities.
The embodiment also provides a preparation method of the steel for the package removal of the high-yield one-time cold-rolled cover, which comprises the following steps:
s1, obtaining a casting blank of the high-yield primary cold-rolled cover unpacking steel;
s2, sequentially carrying out hot rolling, acid washing, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover-annealing packaging,
the hot rolling procedure comprises the steps of casting blank heating, rough rolling, finish rolling and coiling:
in the process of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be 15 ℃, the heating temperature of the casting blank is controlled to be 1217 ℃, the heating time is controlled to be 3.0h,
in rough rolling, rolling is carried out by adopting 3+5 passes, and the total deformation of the rough rolling is controlled to be 85%;
in the fine rolling, 7 passes are adopted for rolling, the rolling speed is controlled to be 14mm/s, the total deformation of the fine rolling is controlled to be 93 percent, the outlet temperature of the fine rolling is 887 ℃,
the coiling temperature is 561 ℃;
in the cold rolling, the cold rolling reduction is controlled to be 89%, and the thickness of the cold-rolled plate obtained by the cold rolling is controlled to be 0.22 mm;
in the cover annealing, the annealing temperature is controlled to be 625 ℃, and the heat preservation time is controlled to be 11 h;
the flat elongation was 2.0%.
In this example, the thickness of the high yield steel for one-time cold rolling cover unpacking is 0.22mm, and the metallographic structure of the steel is, in terms of volume fraction: 97% of ferrite and 3% of cementite, wherein the grain size of the ferrite is 5.0 mm.
Example 4
The high-yield steel for once cold-rolled cap unpacking comprises the following chemical components in percentage by mass:
c: 0.050%, Si: 01%, Mn: 0.20%, P: 0.01%, S: 0.008%, Als: 0.006%, N: 0.016% and the balance of Fe and inevitable impurities.
The embodiment also provides a preparation method of the steel for the package removal of the high-yield one-time cold-rolled cover, which comprises the following steps:
s1, obtaining a casting blank of the high-yield primary cold-rolled cover unpacking steel;
s2, sequentially carrying out hot rolling, acid washing, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover-annealing packaging,
the hot rolling procedure comprises the steps of casting blank heating, rough rolling, finish rolling and coiling:
in the process of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be 15 ℃, the heating temperature of the casting blank is controlled to be 1180 ℃, the heating time is controlled to be 2.6 hours,
in rough rolling, rolling is carried out by adopting 0+5 passes, and the total deformation of the rough rolling is controlled to be 84%;
in the fine rolling, 7-pass rolling is adopted, the rolling speed is controlled to be 10.5mm/s, the total deformation of the fine rolling is controlled to be 92 percent, the outlet temperature of the fine rolling is 896 ℃,
coiling temperature is 550 ℃:
in the cold rolling, the cold rolling reduction is controlled to be 81 percent, and the thickness of the cold-rolled plate obtained by the cold rolling is controlled to be 0.49 mm;
in the cover annealing, the annealing temperature is controlled to be 610 ℃, and the heat preservation time is controlled to be 10.5 h;
the flat elongation was 2.0%.
In this example, the thickness of the high yield steel for one-time cold rolling cover unpacking is 0.49mm, and the metallographic structure of the steel is, in terms of volume fraction: 99% ferrite, 1% cementite, wherein the grain size of the ferrite is 5.9 mm.
Example 5
The high-yield steel for once cold-rolled cap unpacking comprises the following chemical components in percentage by mass:
c: 0.075%, Si: 0.02%, Mn: 0.40%, P: 0.015%, S: 0.012%, Als: 0.015%, N: 0.019%, and the balance of Fe and inevitable impurities.
The embodiment also provides a preparation method of the steel for the package removal of the high-yield one-time cold-rolled cover, which comprises the following steps:
s1, obtaining a casting blank of the high-yield primary cold-rolled cover unpacking steel;
s2, sequentially carrying out hot rolling, acid washing, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover-annealing packaging,
the hot rolling procedure comprises the steps of casting blank heating, rough rolling, finish rolling and coiling:
in the process of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be 20 ℃, the heating temperature of the casting blank is controlled to be 1240 ℃, the heating time is controlled to be 4.0h,
in rough rolling, 1+5 passes of rolling are adopted, and the total deformation of the rough rolling is controlled to be 85%;
in the fine rolling, 7-pass rolling is adopted, the rolling speed is controlled to be 15.5mm/s, the total deformation of the fine rolling is controlled to be 95 percent, the outlet temperature of the fine rolling is 860 ℃,
the coiling temperature is 640 ℃:
in the cold rolling, the cold rolling reduction is controlled to be 91%, and the thickness of the cold rolled plate obtained by the cold rolling is controlled to be 0.17 mm:
in the cover type annealing, the annealing temperature is controlled to be 640 ℃, and the heat preservation time is controlled to be 13.8 hours;
the flat elongation was 2.5%.
In this example, the thickness of the high yield steel for one-time cold rolling cover unpacking is 0.17mm, and the metallographic structure of the steel is, in terms of volume fraction: 97% of ferrite and 3% of cementite, wherein the grain size of the ferrite is 4.2 mm.
Comparative example 1
This comparative example differs from example 1 in that: the chemical composition of the steel does not contain N.
Comparative example 2
This comparative example differs from example 1 in that: and Als: 0.02%, N: 0.01 percent.
Comparative example 3
This comparative example differs from example 1 in that:
C：0.03％，Si：0.02％，Mn：0.1％，P：0.015％，S：0.012％，Als：0.004％，N：0.01％。
comparative example 4
This comparative example differs from example 1 in that:
C：0.1％，Si：0.02％，Mn：0.6％，P：0.015％，S：0.012％，Als：0.02％，N：0.025％。
comparative example 5
In this comparative example, the metallographic structure of the steel was, in terms of volume fraction: 99.5% ferrite, 0.5% cementite.
Comparative example 6
In this comparative example, the grain size of ferrite was 3.8 mm.
Related experiments:
the steels obtained in examples 1 to 5 and comparative examples 1 to 6 were subjected to property tests, and the test results are shown in Table 1.
TABLE 1
In the case of the attenuation 1, the optical fiber,
the yield strength refers to the yield limit of a metal material when yielding phenomenon occurs, namely the stress resisting micro plastic deformation, and when the stress is larger than the limit, a part can generate permanent deformation under the action of external force;
yield ratio refers to the ratio of yield point (yield strength) to tensile strength of a material, a too high yield ratio being a brittle failure of the structure, which is strictly prohibited in civil engineering because the structure fails without significant deformation or deformation at failure, which is difficult to prevent:
the three-dimensional strength difference refers to the extremely poor yield strength in the rolling direction, 45-degree direction and transverse direction.
As can be seen from the data in examples 1-5, the high yield steel for the one-time cold rolling cage depacketizing provided by the embodiment of the invention has the advantages of high yield, low yield ratio and small anisotropy.
In comparative example 1, the chemical composition of the steel does not contain N, resulting in a significant reduction in yield strength;
in comparative example 2, having Als above a maximum of 0.018% and N below a minimum of 0.0150% resulted in a significant reduction in yield strength;
in comparative example 3, C, Mn, Als, and N were all below the minimum values, resulting in a significant reduction in yield strength;
in comparative example 4, C, Mn, Als, and N were all higher than the maximum, resulting in a significant decrease in yield strength;
in comparative example 5, the metallographic structure of the steel had too much ferrite content, resulting in a high yield ratio and a large anisotropy;
in comparative example 6, the grain size was too low, resulting in a high yield ratio and a large anisotropy.
Finally, it should also be noted that the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (5)
1. The high-yield steel for the once cold-rolled cap depacketizing is characterized by comprising the following chemical components in percentage by mass:
c: 0.045-0.08%, Si is less than or equal to 0.02%, Mn: 0.15-0.45%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.005-0.018%, N: 0.0150-0.020%, and the balance of Fe and inevitable impurities, wherein the metallographic structure of the steel comprises the following components in percentage by volume: 97-99% of ferrite, 1-3% of cementite, the ferrite having a thickness direction grain size of 4.0-6.0 μm, the steel being prepared by a method comprising:
obtaining a casting blank of the high-yield one-time cold-rolled cover unpacking steel;
sequentially carrying out hot rolling, pickling, cold rolling, cover annealing and leveling on the casting blank to obtain the high-yield steel for the primary cold-rolled cover annealing packaging,
the hot rolling procedure comprises the steps of heating a casting blank, rough rolling, finish rolling and coiling, wherein the heating temperature of the casting blank is 1180-,
in the process of heating the casting blank, the temperature difference of the section of the casting blank is controlled to be less than or equal to 20 ℃, and the heating time is controlled to be 2.5-4.0 h;
in the cover annealing, the annealing temperature is 610-640 ℃, the heat preservation time is controlled to be 10-14h,
the flat elongation is 1.0-2.5%.
2. The high yield steel for the one-time cold rolling cage depackage according to claim 1, wherein the chemical composition of the steel is as follows by mass fraction:
c: 0.050-0.075%, Si not more than 0.02%, Mn: 0.20-0.40%, P is less than or equal to 0.015%, S is less than or equal to 0.012%, Als: 0.006-0.015%, N: 0.0160-0.0190% and the balance of Fe and inevitable impurities.
3. The high yield steel for the one-time cold rolling cage depackage as claimed in claim 1, wherein in the rough rolling, 5 to 8 passes of rolling are adopted, and the total deformation of the rough rolling is controlled to be 83 to 86 percent.
4. The steel for the once-through cold rolling cage depackage of high yield as claimed in claim 1, wherein in the finish rolling, 7 passes are adopted for rolling, the rolling speed is controlled to be 10-16m/s, the total deformation amount of the finish rolling is controlled to be 92-95%, and the outlet temperature of the finish rolling is 850-.
5. The high yield steel for one-time cold rolling cage depacking as claimed in claim 1, wherein in the cold rolling, the cold rolling reduction is controlled to be 80-92%, and the thickness of the cold rolled plate obtained by the cold rolling is controlled to be 0.17-0.50 mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011044915.4A CN112301272B (en) | 2020-09-28 | 2020-09-28 | High-yield steel for one-time cold rolling cover unpacking and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011044915.4A CN112301272B (en) | 2020-09-28 | 2020-09-28 | High-yield steel for one-time cold rolling cover unpacking and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112301272A CN112301272A (en) | 2021-02-02 |
| CN112301272B true CN112301272B (en) | 2022-04-19 |
Family
ID=74489166
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011044915.4A Active CN112301272B (en) | 2020-09-28 | 2020-09-28 | High-yield steel for one-time cold rolling cover unpacking and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112301272B (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111763876A (en) * | 2019-04-02 | 2020-10-13 | 上海梅山钢铁股份有限公司 | Cold-rolled steel plate for motor vehicle silencing sheet and production method thereof |
| CN113373375B (en) * | 2021-05-26 | 2022-07-19 | 攀钢集团攀枝花钢铁研究院有限公司 | 600 MPa-grade hot-rolled automobile beam steel strip with high fatigue performance and preparation method thereof |
| CN113322413B (en) * | 2021-05-28 | 2022-07-19 | 攀钢集团攀枝花钢铁研究院有限公司 | High-fatigue-performance 900 MPa-grade hot-rolled automobile crossbeam steel strip and preparation method thereof |
| CN113308646B (en) * | 2021-05-28 | 2022-07-19 | 攀钢集团攀枝花钢铁研究院有限公司 | High-fatigue-performance 700 MPa-grade hot-rolled automobile crossbeam steel strip and preparation method thereof |
| CN113322416B (en) * | 2021-05-31 | 2022-07-19 | 攀钢集团攀枝花钢铁研究院有限公司 | 800 MPa-grade hot-rolled automobile beam steel strip with high fatigue performance and preparation method thereof |
| CN114807771B (en) * | 2022-04-14 | 2023-10-31 | 首钢集团有限公司 | Thin strip steel with large width-to-thickness ratio and preparation method and application thereof |
| CN116716539A (en) * | 2023-04-28 | 2023-09-08 | 邯郸市金泰包装材料有限公司 | Cracking-resistant hard tin plate suitable for flower basket barrel and manufacturing method thereof |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2016067514A1 (en) * | 2014-10-28 | 2016-05-06 | Ｊｆｅスチール株式会社 | Steel sheet for two-piece can and manufacturing method therefor |
| WO2016157877A1 (en) * | 2015-03-31 | 2016-10-06 | Ｊｆｅスチール株式会社 | Steel sheet for can lids and method for producing same |
| CN104928576A (en) * | 2015-05-13 | 2015-09-23 | 唐山钢铁集团有限责任公司 | Production method of 260-330MPa low-alloy high-strength steel |
| CN107916371A (en) * | 2017-11-24 | 2018-04-17 | 攀钢集团攀枝花钢铁研究院有限公司 | The production method of glassed steel |
| CN110983179A (en) * | 2019-12-16 | 2020-04-10 | 首钢集团有限公司 | Steel for one-time cold rolling and continuous annealing packaging and preparation method thereof |
-
2020
- 2020-09-28 CN CN202011044915.4A patent/CN112301272B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN112301272A (en) | 2021-02-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112301272B (en) | High-yield steel for one-time cold rolling cover unpacking and preparation method thereof | |
| KR101638719B1 (en) | Galvanized steel sheet and method for manufacturing the same | |
| CN104946969B (en) | Hot-rolled pickled steel plate for air conditioner compressor housings and manufacturing method thereof | |
| KR20140105849A (en) | Ferrite-austenite 2-phase stainless steel plate having low in-plane anisotropy and method for producing same | |
| EP3719160B1 (en) | Non-oriented electrical steel sheet with excellent magnetism and manufacturing method therefor | |
| CN105112776A (en) | Phosphorus-containing low-carbon cold-rolled hard tin-plated steel plate and production method thereof | |
| KR20130023274A (en) | Cold-rolled thin steel sheet having excellent shape fixability, and process for production thereof | |
| WO2017043660A1 (en) | Steel sheet and enameled product | |
| KR20130083487A (en) | High-strength steel sheet for container and process for production thereof | |
| KR101128315B1 (en) | Processes for production of steel sheets for cans | |
| CN113774274B (en) | Low-cost well-formed battery case steel and production method thereof | |
| CN107557679A (en) | Lightweight austenitic steel and its production method with good strong plasticity | |
| CN109694990A (en) | Light phase transition inducing plasticity steel and its production method with good strong plasticity | |
| CN110819906A (en) | Method for improving deep drawing performance of cold-rolled strip steel with deteriorated residual elements of Cu, As and Sn | |
| CN110629000A (en) | Cold-rolled hot-dip galvanized steel sheet with yield strength of 280MPa and manufacturing method thereof | |
| CN110904392A (en) | Ultra-low carbon anti-pressure thin-specification cold-rolled sheet for battery shell and production method thereof | |
| CN102418047B (en) | Non-quenched and tempered fatigue-resistant steel plate and manufacturing method thereof | |
| EP0071270A1 (en) | Process for producing an austenitic stainless steel sheet or strip | |
| CN107829026B (en) | thin-specification 980 MPa-grade dual-phase steel and processing method thereof | |
| JP2007177303A (en) | Steel having excellent ductility and its production method | |
| CN112501513B (en) | Low-carbon acid-pickled steel with excellent formability and surface quality and production method thereof | |
| CN107829025B (en) | thin-gauge dual-phase steel with good hole expanding performance and processing method thereof | |
| CN111636031A (en) | Ultra-low carbon bake-hardening steel and production method thereof | |
| CN111534757A (en) | Steel for packaging, production method thereof and packaging product | |
| CN111763875A (en) | High-hardness cold-rolled electrotinning substrate for bottle cap and production 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 |