CN114959449A - Production method of low-yield-ratio chromium-molybdenum alloy steel - Google Patents
Production method of low-yield-ratio chromium-molybdenum alloy steel Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 75
- 239000010959 steel Substances 0.000 title claims abstract description 75
- 229910001182 Mo alloy Inorganic materials 0.000 title claims abstract description 24
- VNTLIPZTSJSULJ-UHFFFAOYSA-N chromium molybdenum Chemical compound [Cr].[Mo] VNTLIPZTSJSULJ-UHFFFAOYSA-N 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title abstract description 20
- 238000005096 rolling process Methods 0.000 claims abstract description 54
- 238000005266 casting Methods 0.000 claims abstract description 14
- 238000010438 heat treatment Methods 0.000 claims abstract description 12
- 239000002893 slag Substances 0.000 claims abstract description 9
- 238000007670 refining Methods 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 6
- 238000001953 recrystallisation Methods 0.000 claims description 20
- 238000000034 method Methods 0.000 claims description 19
- 238000010079 rubber tapping Methods 0.000 claims description 11
- 239000011651 chromium Substances 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 7
- 238000009749 continuous casting Methods 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 3
- 229910000851 Alloy steel Inorganic materials 0.000 claims description 2
- 230000014759 maintenance of location Effects 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 238000005516 engineering process Methods 0.000 abstract description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical group [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 7
- 238000005336 cracking Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 239000000788 chromium alloy Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000001624 sedative effect Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
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- 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
- 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
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- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- 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
- 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
-
- 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
- C21D2211/009—Pearlite
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Heat Treatment Of Steel (AREA)
Abstract
The application provides a production method of chromium-molybdenum alloy steel with a low yield ratio, which comprises the following steps: smelting in a converter, and controlling the C content in the steel to be more than or equal to 0.06 percent and the P content to be less than or equal to 0.015 percent; LF refining, keeping the white slag for more than or equal to 15min, and controlling the S content in the steel to be less than or equal to 0.010 percent; continuously casting the plate blank, namely casting the plate blank by adopting the steel obtained in the step two, wherein the thickness of the plate blank is 150 mm; the slab is cooled in a heaping way, and the slab heaping time is more than or equal to 24 hours; heating the plate blank, and controlling the temperature to 1150-1280 ℃; and (4) controlling rolling, namely controlling rolling in two stages to finally obtain a steel plate finished product. The invention adopts microalloying technology, and produces the chrome-molybdenum alloy steel with the yield ratio of less than or equal to 0.60 by controlled rolling, the yield strength is more than or equal to 300MPa, the tensile strength is more than or equal to 450MPa, the elongation after fracture is more than or equal to 20 percent, and the transverse 20 ℃ impact of the steel plate is more than or equal to 100J.
Description
Technical Field
The invention relates to the technical field of steel production, in particular to a production method of low-yield-ratio chromium-molybdenum alloy steel.
Background
Along with the rapid development of national economy, the demand on the strength of a steel plate is higher and higher, the yield ratio is an important index for measuring the safety of structural parts, high-yield-ratio steel can be broken quickly after yielding, low-yield-ratio steel can be subjected to larger strain strengthening after yielding, the steel can be broken only when reaching higher tensile strength, and bridge design units require that the yield ratio of bridge steel is less than or equal to 0.85. In addition, with the addition of Mo and Cr, the yield ratio is more and more difficult to control.
The patent CN101215624B discloses an on-line quenching production process method of a high-strength and high-toughness thick steel plate, which utilizes on-line quenching and high-temperature tempering to obtain the high-strength and high-toughness thick steel plate, and does not realize yield ratio control.
The invention CN103422021A discloses a low yield ratio structural steel with yield strength more than or equal to 550MPa, which comprises the components of 0.10 to 0.40 percent of Cr0.10 and 0.10 to 0.50 percent of Mo0.80 percent of CrZ and the yield ratio less than or equal to 0.80.
The invention CN104789892A discloses a low yield ratio and high toughness thick steel plate with excellent low temperature impact toughness, which comprises the components of 0.20 to 0.07 percent of Cr0, 0.20 to 0.80 percent of Mo0 and 0.62 to 0.64 percent of yield ratio.
The invention CN 112501496A discloses an on-line quenching type double-phase low yield strength steel plate and a production method thereof. The invention realizes the good balance of the strength and the yield ratio of the 370-420 MPa grade bridge steel with the thickness less than or equal to 24mm, and the invention patent is 0.62-0.74, but the components do not contain alloy elements Cr and Mo.
The chromium-molybdenum alloy steel has a high yield ratio which reaches 0.80-0.90. The company fully applies microalloy technology to steel materials by means of self technology, regulates and controls the proportion of main hardenability elements C-Mn-Cr-Mo, adopts a full-flow grain refining production process to manufacture molybdenum-chromium alloy steel with the yield ratio less than or equal to 0.60, effectively promotes the production of high-strength steel and the development of downstream industries, and therefore, provides a production method of chromium-molybdenum alloy steel with low yield ratio to solve the problems.
Disclosure of Invention
The invention mainly aims to provide a production method of chromium-molybdenum alloy steel with low yield ratio, which can effectively solve the problems in the background technology.
In order to achieve the purpose, the invention adopts the technical scheme that:
a production method of chromium-molybdenum alloy steel with low yield ratio comprises the following steps: a production method of a chromium-molybdenum alloy steel plate comprises the following chemical components in percentage by mass: c: 0.15 to 0.18%, Si: 0.20 to 0.40%, Mn: 0.50-0.70%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, Alt is less than or equal to 0.050%, N is less than or equal to 0.0080%, Ni is less than or equal to 0.30%, and Cr: 0.90-1.20%, Mo: 0.45-0.60%, and the balance of Fe and unavoidable elements;
a production method of chromium-molybdenum alloy steel with low yield ratio comprises the following steps:
firstly, smelting in a converter, wherein C contained in steel tapping is controlled to be more than or equal to 0.06 percent, and P is controlled to be less than or equal to 0.015 percent;
step two, LF refining, wherein the white slag retention time is more than or equal to 15min, and the S contained in the steel is controlled to be less than or equal to 0.010%;
step three, slab continuous casting, wherein the steel obtained in the step two is adopted to cast a slab, and the thickness of the slab is 150 mm;
step four, stacking and cooling the plate blank, wherein the stacking and cooling time of the plate blank is more than or equal to 24 hours;
fifthly, heating the plate blank, and controlling the temperature to 1150-1280 ℃;
and step six, rolling control, namely rolling control in two stages.
Preferably, in the second step, the whole process is protected for casting, and the casting temperature is controlled according to the liquidus temperature of +10 to +25 ℃.
Preferably, in the fifth step, a walking beam furnace is used for heating.
Preferably, in the sixth step, the two-stage controlled rolling is divided into a first-stage controlled rolling and a second-stage controlled rolling, wherein,
the first stage controlled rolling comprises the following steps: rolling in a recrystallization zone, wherein the temperature range is 980-1120 ℃;
and a second stage: rolling temperature interval of non-recrystallization zone: the initial rolling temperature is 840-960 ℃, and the final rolling temperature is 760-880 ℃.
Preferably, the rolling pass reduction rate of the recrystallization zone is more than or equal to 15 percent, and the rolling total reduction rate of the unrecrystallized zone is more than or equal to 50 percent.
Compared with the prior art, the invention has the following beneficial effects:
the invention adopts microalloying technology, and produces the chrome-molybdenum alloy steel with the yield ratio of less than or equal to 0.60 by controlled rolling, the yield strength is more than or equal to 300MPa, the tensile strength is more than or equal to 450MPa, the elongation after fracture is more than or equal to 20 percent, and the transverse 20 ℃ impact of the steel plate is more than or equal to 100J.
Drawings
FIG. 1 is a process flow chart of a method for producing a low yield ratio chromium molybdenum alloy steel of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be obtained by a person skilled in the art without making any creative effort based on the embodiments in the present invention, belong to the protection scope of the present invention.
Example 1:
the production method of the low yield ratio chromium-molybdenum alloy steel comprises the following steps of:
step one, smelting in a converter: controlling the tapping C to be more than or equal to 0.06 percent and the tapping P to be less than or equal to 0.015 percent; slag falling in the tapping process is avoided;
step two, LF refining: the white slag is kept for more than 15min, and S is controlled to be less than or equal to 0.010%;
step three, slab continuous casting: the thickness of the casting blank is 150mm, the casting is protected in the whole process, and the casting temperature is controlled according to the liquidus temperature plus 10 to plus 25 ℃;
step four, slab stacking and cooling: the slab is cooled in a heaped mode for not less than 24 hours;
step five, heating the plate blank: a walking beam type heating furnace is adopted, and the temperature is controlled to be 1150-1280 ℃;
step six, rolling control: the rolling is controlled by adopting two stages, wherein the first stage comprises the following steps: rolling temperature interval of recrystallization zone: 980-1120 ℃, and the rolling pass reduction rate of the recrystallization zone is more than or equal to 15%; and a second stage: rolling temperature interval of non-recrystallization zone: the initial rolling temperature is 840-960 ℃, the rolling total reduction rate of a non-recrystallization area is more than or equal to 50%, and the final rolling temperature is 760-880 ℃;
in the present example, the metallographic structure of the steel sheet was ferrite and pearlite.
In the embodiment, the performance indexes of the production method for producing the low yield ratio steel plate by adopting the chromium-molybdenum alloy are shown in table 2.
Table 1 example 1 steel sheet composition (wt%)
| C | Si | Mn | P | S | Al | Cr | Mo | N | CEV |
| 0.151 | 0.25 | 0.62 | 0.014 | 0.006 | 0.03 | 1.07 | 0.466 | 0.0049 | 0.57 |
TABLE 1
Note: CEV is carbon equivalent and is calculated by the formula: CEV: c + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15.
TABLE 2 Process and Performance indicators for example 1
TABLE 2
Example 2:
the production method of the low yield ratio chromium-molybdenum alloy steel comprises the following steps of:
step one, smelting in a converter: controlling the tapping C to be more than or equal to 0.06 percent and the tapping P to be less than or equal to 0.015 percent; slag falling in the tapping process is avoided;
step two, LF refining: the white slag is kept for more than 15min, and S is controlled to be less than or equal to 0.010 percent;
step three, slab continuous casting: the thickness of the casting blank is 150mm, the casting is protected in the whole process, and the casting temperature is controlled according to the liquidus temperature plus 10 to plus 25 ℃;
step four, stacking and cooling the plate blank: the slab is cooled in a heaped mode for not less than 24 hours;
step five, heating the plate blank: a walking beam type heating furnace is adopted, and the temperature is controlled to be 1150-1280 ℃;
step six, controlled rolling: the rolling is controlled by adopting two stages, wherein the first stage comprises the following steps: rolling temperature interval of recrystallization zone: 980-1120 ℃, and the rolling pass reduction rate of the recrystallization zone is more than or equal to 15%;
and a second stage: rolling temperature interval of non-recrystallization zone: the initial rolling temperature is 840-960 ℃, the rolling total reduction rate of the non-recrystallization zone is more than or equal to 50%, and the final rolling temperature is 760-880 ℃;
in the present example, the metallographic structure of the steel sheet was ferrite and pearlite.
In this example, the performance index of the low yield ratio steel plate produced by using the chromium molybdenum alloy is shown in table 4.
Table 3 example 2 steel plate composition (wt%)
| C | Si | Mn | P | S | Al | Cr | Mo | N | CEV |
| 0.152 | 0.25 | 0.61 | 0.014 | 0.006 | 0.03 | 1.05 | 0.464 | 0.0049 | 0.57 |
TABLE 3
Note: CEV is carbon equivalent and is calculated by the formula: CEV: c + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15.
Table 4 example 2 performance index
TABLE 4
Example 3:
the chemical components and the mass percent of the steel plate are shown in a table 5, and the process steps of the steel plate production method comprise the following steps:
step one, smelting in a converter: controlling the tapping C to be more than or equal to 0.06 percent and the tapping P to be less than or equal to 0.015 percent; slag falling in the tapping process is avoided;
step two, LF refining: the white slag is kept for more than 15min, and S is controlled to be less than or equal to 0.010 percent;
step three, slab continuous casting: the thickness of the casting blank is 150mm, the casting is protected in the whole process, and the casting temperature is controlled according to the liquidus temperature plus 10 to plus 25 ℃;
step four, slab stacking and cooling: the slab is cooled in a heaped mode for not less than 24 hours;
step five, heating the plate blank: a walking beam type heating furnace is adopted, and the temperature is controlled to be 1150-1280 ℃;
step six, rolling control: the rolling is controlled by adopting two stages, wherein the first stage comprises the following steps: rolling temperature interval of recrystallization zone: 980-1120 ℃, and the rolling pass reduction rate of the recrystallization zone is more than or equal to 15%; and a second stage: rolling temperature interval of non-recrystallization zone: the initial rolling temperature is 840-960 ℃, the rolling total reduction rate of a non-recrystallization area is more than or equal to 50%, and the final rolling temperature is 760-880 ℃;
in the present example, the metallographic structure of the steel sheet was ferrite and pearlite.
In this example, the performance index of the chromium molybdenum alloy steel sheet with low yield ratio is shown in table 6.
TABLE 5 example 3 Steel sheet composition (wt%)
| C | Si | Mn | P | S | Al | Cr | Mo | N | CEV |
| 0.150 | 0.25 | 0.63 | 0.014 | 0.006 | 0.03 | 1.07 | 0.468 | 0.0050 | 0.57 |
TABLE 5
Note: CEV is carbon equivalent, and the calculation formula is: CEV: c + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15.
Table 6 example 3 performance index
TABLE 6
As can be seen from the above examples, the steel sheet produced in example 3 has the best performance index and low yield ratio.
The working principle of the invention is as follows:
c: the carbon content is one of main elements for improving the strength of steel, the yield strength and the tensile strength of steel are improved along with the increase of the carbon content, but the elongation and the impact toughness of the steel are reduced along with the increase of the carbon content, and when the steel with higher C content is welded, the hardening phenomenon can also occur in a welding heat affected zone, which will aggravate the tendency of cold cracking during welding, so that the carbon content of 0.15-0.18% is adopted;
si: it is helpful for improving the strength of steel, and has a sedative effect;
mn: the steel plate is a solid solution strengthening element, and is beneficial to improving the strength of the steel plate;
p: the steel has a cold brittleness tendency, and the content of the steel is as low as possible;
s: the steel has a hot cracking tendency, and the content of the steel is required to be as low as possible;
n: the steel has a hot cracking tendency, and the content of the steel is as low as possible;
al: the method is mainly used for deoxidizing and refining grains;
cr: the solid solution strengthening effect is achieved, and the oxidation resistance and heat resistance of the steel can be improved;
mo: the high carbide forming ability can obviously improve the recrystallization temperature of steel, improve the tempering stability and inhibit the brittleness of alloy steel caused by tempering.
The foregoing shows and describes the general principles and broad features of the present invention and advantages thereof. It will be understood by those skilled in the art that the present invention is not limited to the embodiments described above, which are given by way of illustration of the principles of the present invention, but that various changes and modifications may be made without departing from the spirit and scope of the invention, and such changes and modifications are within the scope of the invention as claimed. The scope of the invention is defined by the appended claims and equivalents thereof.
Claims (6)
1. The low yield ratio chromium molybdenum alloy steel is characterized in that: the alloy steel comprises the following chemical components in percentage by mass: c: 0.15 to 0.18%, Si: 0.20 to 0.40%, Mn: 0.50-0.70%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, Alt is less than or equal to 0.050%, N is less than or equal to 0.0080%, Ni is less than or equal to 0.30%, and Cr: 0.90-1.20%, Mo: 0.45-0.60%, and the balance of Fe element and unavoidable elements.
2. A method of producing a low yield ratio chromium molybdenum alloy steel according to claim 1, characterised in that: the method comprises the following steps:
firstly, smelting in a converter, wherein C contained in steel tapping is controlled to be more than or equal to 0.06 percent, and P is controlled to be less than or equal to 0.015 percent;
step two, LF refining, wherein the white slag retention time is more than or equal to 15min, and the S contained in the steel is controlled to be less than or equal to 0.010%;
step three, slab continuous casting, wherein the steel obtained in the step two is adopted to cast a slab, and the thickness of the slab is 150 mm;
step four, stacking and cooling the plate blank, wherein the stacking and cooling time of the plate blank is more than or equal to 24 hours;
fifthly, heating the plate blank, and controlling the temperature to 1150-1280 ℃;
and step six, rolling control, namely, rolling control in two stages to finally obtain a steel plate finished product.
3. A method of producing a low yield ratio chromium molybdenum alloy steel according to claim 2, characterised in that: in the second step, the whole process is protected and cast, and the casting temperature is controlled according to the liquidus temperature plus 10 to plus 25 ℃.
4. A method of producing a low yield ratio chromium molybdenum alloy steel according to claim 2, characterised in that: and in the fifth step, a walking beam type heating furnace is adopted for heating.
5. A method of producing a low yield ratio chromium molybdenum alloy steel according to claim 1, characterised in that: in the sixth step, the two-stage controlled rolling is divided into a first-stage controlled rolling and a second-stage controlled rolling, wherein,
the first stage controlled rolling comprises the following steps: rolling in a recrystallization zone, wherein the temperature range is 980-1120 ℃;
the second stage controlled rolling comprises the following steps: rolling temperature interval of non-recrystallization zone: the initial rolling temperature is 840-960 ℃, and the final rolling temperature is 760-880 ℃.
6. A method of producing a low yield ratio chromium molybdenum alloy steel according to claim 5, characterised in that: the pass reduction rate of the recrystallization zone rolling is more than or equal to 15 percent, and the total rolling reduction rate of the non-recrystallization zone rolling is more than or equal to 50 percent.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007197823A (en) * | 2005-12-28 | 2007-08-09 | Jfe Steel Kk | LOW YIELD RATIO OF 550 MPa CLASS HIGH-TENSILE STEEL PLATE, AND ITS MANUFACTURING METHOD |
| CN102796957A (en) * | 2012-08-31 | 2012-11-28 | 济钢集团有限公司 | Steel plate for high toughness 15CrMoR pressure container |
| CN103334064A (en) * | 2013-06-21 | 2013-10-02 | 舞阳钢铁有限责任公司 | Low yield ratio chromium-molybdenum steel plate and production method thereof |
| CN105861924A (en) * | 2016-05-31 | 2016-08-17 | 舞阳钢铁有限责任公司 | Low-alloy 15CrMo steel plate and production method thereof |
| CN106834940A (en) * | 2017-01-18 | 2017-06-13 | 舞阳钢铁有限责任公司 | Pressure vessel hydrogen sulphide-corrosion-resistant low alloy high strength steel plate and production method |
| KR20210000844A (en) * | 2019-06-26 | 2021-01-06 | 현대제철 주식회사 | Pressure vessel steel sheet excellent in pwhthresistance and menufacturing mwthod thereof |
-
2022
- 2022-04-22 CN CN202210428362.5A patent/CN114959449A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007197823A (en) * | 2005-12-28 | 2007-08-09 | Jfe Steel Kk | LOW YIELD RATIO OF 550 MPa CLASS HIGH-TENSILE STEEL PLATE, AND ITS MANUFACTURING METHOD |
| CN102796957A (en) * | 2012-08-31 | 2012-11-28 | 济钢集团有限公司 | Steel plate for high toughness 15CrMoR pressure container |
| CN103334064A (en) * | 2013-06-21 | 2013-10-02 | 舞阳钢铁有限责任公司 | Low yield ratio chromium-molybdenum steel plate and production method thereof |
| CN105861924A (en) * | 2016-05-31 | 2016-08-17 | 舞阳钢铁有限责任公司 | Low-alloy 15CrMo steel plate and production method thereof |
| CN106834940A (en) * | 2017-01-18 | 2017-06-13 | 舞阳钢铁有限责任公司 | Pressure vessel hydrogen sulphide-corrosion-resistant low alloy high strength steel plate and production method |
| KR20210000844A (en) * | 2019-06-26 | 2021-01-06 | 현대제철 주식회사 | Pressure vessel steel sheet excellent in pwhthresistance and menufacturing mwthod thereof |
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