CN113802066A - B600B high-strength steel bar and production process thereof - Google Patents
B600B high-strength steel bar and production process thereof Download PDFInfo
- Publication number
- CN113802066A CN113802066A CN202111101627.2A CN202111101627A CN113802066A CN 113802066 A CN113802066 A CN 113802066A CN 202111101627 A CN202111101627 A CN 202111101627A CN 113802066 A CN113802066 A CN 113802066A
- Authority
- CN
- China
- Prior art keywords
- billet
- rolling
- finish
- steel bar
- steel
- 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.)
- Pending
Links
Images
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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- 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
- C21D2211/008—Martensite
Abstract
The invention provides a B600B high-strength steel bar and a production process thereof, wherein the high-strength steel bar comprises the following chemical components in percentage by weight: c: 0.17-0.22%, Mn: 1.00-1.20%, Si: 0.40-0.55%, V: 0.025-0.045%, P is less than or equal to 0.048%, S is less than or equal to 0.048%, Cr: 0.31-0.45%, and the balance of Fe and inevitable impurities. The carbon equivalent Ceq of the high-strength steel bar is 0.44-0.50%. The mechanical property Re of the high-strength steel bar is 625-780MPa, the yield ratio is not less than 1.08, and Agt is not less than 5.0%. According to the invention, the high-strength steel bar meeting the mechanical property is obtained by controlling the contents of C, Si, Mn, V and Cr elements and rolling the smelted steel billet.
Description
Technical Field
The invention relates to the field of metallurgy or high-strength steel bars, in particular to a B600B high-strength steel bar and a production process thereof.
Background
Singapore Standard B600B high strength rebar is widely used in various building structures, particularly large, heavy, light, thin-walled and high-rise building structures. Compared with the steel bar of 400MPa grade, the steel amount can be saved by more than 30% by adopting the B600B grade and above high-strength steel bar. The development and application of the novel material can also promote the popularization and application of the novel material with high performance, energy conservation and environmental protection, greatly improve the variety and structure of the current products for construction, and provide powerful support for resource-saving and environment-friendly enterprises.
However, the currently produced B600B high-strength steel bar is mainly produced by a high microalloy + hot rolling process, and the ratio of V: 0.15-0.17%, Si: 0.65-0.80%, and high cost due to high content of V and Si.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides the B600B high-strength steel bar and the production process thereof, and the high-strength steel bar meeting the mechanical property is obtained by controlling the contents of C, Si, Mn, V and Cr elements and rolling the smelted steel billet, and the production cost is reduced.
The present invention achieves the above-described object by the following technical means.
A B600B high-strength steel bar comprises the following chemical components in percentage by weight:
c: 0.17-0.22%, Mn: 1.00-1.20%, Si: 0.40-0.55%, V: 0.025-0.045%, P is less than or equal to 0.048%, S is less than or equal to 0.048%, Cr: 0.31-0.45%, and the balance of Fe and inevitable impurities.
Further, the carbon equivalent Ceq of the high-strength steel bar is 0.44-0.50%.
Furthermore, the mechanical property Re of the high-strength steel bar is 625-780MPa, the yield ratio is not less than 1.08, and Agt is not less than 5.0%.
A production process of B600B high-strength steel bars comprises the following steps:
refining through a refining furnace to obtain refined molten steel;
rolling the refined molten steel through a continuous casting machine to obtain a continuous casting billet;
conveying the continuous casting billet to a steel rolling heating furnace for heating, and then entering a frame roughing mill set for roughing operation to obtain a roughing billet;
after the rough rolling billet is sheared and broken, the rough rolling billet enters a rack middle rolling unit to perform middle rolling operation, and a middle rolling billet is obtained; after the pre-water cooling section of the medium-rolled steel billet is subjected to low-temperature finish rolling, shearing and breaking are carried out, and the medium-rolled steel billet enters a rack finishing mill group to be subjected to finish rolling operation, so that a finish-rolled steel billet is obtained;
carrying out quenching self-tempering treatment on the finish-rolled steel billet;
and cooling and processing the finish rolling billet.
Further, the quenching self-tempering treatment is carried out on the finish rolling billet, and the quenching self-tempering treatment specifically comprises the following steps:
the surface of the finish rolling steel billet is rapidly cooled by water through the water, the finish rolling steel billet is used for forming a cold hard layer on the surface of the finish rolling steel billet, and the cooling speed of the surface of the finish rolling steel billet is higher than the speed of forming martensite so as to obtain coarse martensite;
the martensite on the quenching surface of the finish-rolled steel slab is self-tempered by the temperature of the core part of the finish-rolled steel slab, and the strength and toughness of the steel are increased by the tempered martensite formed by the self-tempering.
Further, the finish-rolled steel billet is cooled by a cooling bed, the temperature of the cooling bed is controlled between 555-575 ℃, and the unconverted austenite in the core part of the finish-rolled steel billet is subjected to semi-isothermal phase change to provide hardenability.
Further, the temperature of the water passing through the finish rolling billet is not more than 830 ℃.
Further, the heating temperature of the steel rolling heating furnace is controlled at 1000-1050 ℃; the temperature of the rough rolling operation and the medium rolling operation is more than 900 ℃; the temperature of the finish rolling operation is 830-900 ℃.
The invention has the beneficial effects that:
1. according to the B600B high-strength steel bar, the content of each element of C, Si, Mn, V and Cr is controlled, and the smelted steel billet is rolled to obtain the high-strength steel bar with the mechanical properties of Re 625-780MPa, the yield ratio not less than 1.08 and Agt not less than 5.0%.
2. The B600B high-strength steel bar is a well-known economic and effective method for carrying out vanadium and nitrogen microalloying by adding vanadium-nitrogen-gold, and simultaneously, the hardenability of the steel bar can be improved by adding 0.31-0.45% of Cr, so that the phase change and fine grain strengthening effects of the steel bar are enhanced. The addition of 0.025-0.045% of V can not only fully play the reinforcing role of vanadium, but also avoid the waste of alloy resources. The B600B high strength steel bar produced by the patent technology has the cost lower than that of the conventional production by more than 150 yuan, and all indexes meet the requirements, so that the use cost of customers can be greatly reduced, and the market popularization is facilitated.
3. The production method of the B600B high-strength steel bar uses a quenching self-tempering production process, and relies on C (carbon), Si (silicon) and Mn (manganese) in the steel to rapidly quench and cool under the action of high-pressure water, and then relies on the core temperature of the steel bar to realize self-tempering, so that a compact tempering structure is formed on the surface. In order to improve the hardenability of the steel bar, Cr (chromium) is also added into the steel independently, thereby further reducing the addition of Si and Mn and the production cost. After quenching and tempering treatment, the steel-making and continuous casting technology for preventing the surface defects of casting blanks of high-microalloy billets is developed, the microalloy solid solution strengthening, fine grain strengthening, precipitation strengthening and corresponding heating, controlled rolling and controlled cooling rolling technologies are integrated, a stable industrialized rolling technology is formed, the cost is reduced, and the technical effects of greatly improving the economic benefit are achieved.
Drawings
Fig. 1 is a metallographic image of a B600B high-strength steel bar according to example 1 of the present invention, where fig. 1a is a metallographic image of a side structure of example 1, fig. 1B is a metallographic image of a transition structure of example 1, and fig. 1c is a metallographic image of a core structure of example 1.
Fig. 2 is a phase diagram of B600B high-strength steel bar according to embodiment 2 of the present invention, where fig. 2a is a phase diagram of edge structure of embodiment 2, fig. 2B is a phase diagram of transition structure of embodiment 2, and fig. 2c is a phase diagram of core structure of embodiment 2.
Fig. 3 is a phase diagram of B600B high-strength steel bar according to embodiment 3 of the present invention, where fig. 3a is a phase diagram of edge structure of embodiment 3, fig. 3B is a phase diagram of transition structure of embodiment 3, and fig. 3c is a phase diagram of core structure of embodiment 3.
Fig. 4 is a phase diagram of B600B high-strength steel bar according to embodiment 4 of the present invention, where fig. 4a is a phase diagram of edge structure of embodiment 4, and fig. 4B is a phase diagram of core structure of embodiment 4.
Fig. 5 is a metallographic graph of a B600B high-strength steel bar according to embodiment 5 of the present invention, where fig. 5a is a metallographic graph of an edge structure of embodiment 5, and fig. 5B is a metallographic graph of a core structure of embodiment 5.
Fig. 6 is a metallographic graph of a B600B high-strength steel bar according to embodiment 6 of the present invention, where fig. 6a is a metallographic graph of an edge structure of embodiment 6, and fig. 6B is a metallographic graph of a core structure of embodiment 6.
Detailed Description
The invention will be further described with reference to the following figures and specific examples, but the scope of the invention is not limited thereto.
Reference will now be made in detail to embodiments of the present invention, examples of which are illustrated in the accompanying drawings, wherein like or similar reference numerals refer to the same or similar elements or elements having the same or similar function throughout. The embodiments described below with reference to the drawings are illustrative and intended to be illustrative of the invention and are not to be construed as limiting the invention.
In the description of the present invention, it is to be understood that the terms "central," "longitudinal," "lateral," "length," "width," "thickness," "upper," "lower," "axial," "radial," "vertical," "horizontal," "inner," "outer," and the like are used in the orientations and positional relationships indicated in the drawings for convenience in describing the present invention and for simplicity in description, and are not intended to indicate or imply that the referenced devices or elements must have a particular orientation, be constructed and operated in a particular orientation, and are not to be considered limiting. Furthermore, the terms "first", "second" and "first" are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implicitly indicating the number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of the present invention, "a plurality" means two or more unless specifically defined otherwise.
In the present invention, unless otherwise expressly specified or limited, the terms "mounted," "connected," "secured," and the like are to be construed broadly and can, for example, be fixedly connected, detachably connected, or integrally connected; can be mechanically or electrically connected; they may be connected directly or indirectly through intervening media, or they may be interconnected between two elements. The specific meanings of the above terms in the present invention can be understood by those skilled in the art according to specific situations.
The invention relates to a production process of a B600B high-strength steel bar, which comprises the following steps:
step 10: the crude molten steel is obtained by a smelting method.
Step 20: and refining the crude steelmaking water through a refining furnace to obtain refined molten steel.
Step 30: and rolling the refined molten steel through a continuous casting machine to obtain a continuous casting billet.
Step 40: and conveying the continuous casting billet to a heating furnace for heating, and then entering a frame rough rolling unit for rough rolling operation to obtain a rough rolled billet. The temperature of the rough rolling operation is more than 900 DEG C
Before the continuous casting billet is conveyed to a heating furnace for heating, the method comprises the following steps: inspecting the continuous casting billet; and conveying the qualified continuous casting steel billet to the heating furnace for heating through a conveying roller way, wherein the heating temperature of the heating furnace is controlled to be 1000-1050 ℃.
Step 50: and after shearing and breaking the rough rolling billet, feeding the rough rolling billet into a rack medium rolling mill set for medium rolling operation to obtain a medium rolling billet.
The cutting and breaking of the rough rolling billet comprises the following steps: and cutting the rough rolling billet into a billet head and a billet tail by the crank arm, and then cutting the rough rolling billet into pieces. The temperature of the medium rolling operation is more than 900 ℃;
step 60: and (3) performing low-temperature finish rolling on the medium-rolled steel billet at a pre-water cooling section, shearing and breaking the medium-rolled steel billet, and performing finish rolling operation on the medium-rolled steel billet in a rack finishing mill unit to obtain a finish-rolled steel billet. The temperature of the finish rolling operation is 830-900 ℃.
After the pre-water cooling section of the medium rolling billet is subjected to low-temperature finish rolling, shearing and breaking are carried out, and the method comprises the following steps: and performing rotary shearing on the finish rolling billet to cut a billet head and cut a billet tail, and then performing fragmentation.
Step 70: carrying out quenching self-tempering treatment on the finish-rolled steel billet, which specifically comprises the following steps: the surface of the finish rolling steel billet is rapidly cooled by water through the water, the finish rolling steel billet is used for forming a cold hard layer on the surface of the finish rolling steel billet, and the cooling speed of the surface of the finish rolling steel billet is higher than the speed of forming martensite so as to obtain coarse martensite; the temperature of the water passing through the finish rolling billet is not more than 830 ℃.
The martensite on the quenching surface of the finish-rolled steel slab is self-tempered by the temperature of the core part of the finish-rolled steel slab, and the strength and toughness of the steel are increased by the tempered martensite formed by the self-tempering.
Step 80: and cooling the finish rolling billet by a cooling bed, wherein the temperature of the cooling bed is controlled to be between 555-575 ℃ so that the unconverted austenite at the core part of the finish rolling billet is subjected to semi-isothermal phase change to provide hardenability. And finishing and warehousing after shearing.
The principle of the production process is as follows: a quenching self-tempering production process is used, C (carbon), Si (silicon) and Mn (manganese) in steel are quickly quenched and cooled under the action of high-pressure water, and then self-tempering is realized by the core temperature of the steel bar, so that a compact tempering structure is formed on the surface. In order to improve the hardenability of the steel bar, Cr is added into the steel independently, so that the addition amount of Si and Mn and the production cost are further reduced. Combining with chemical composition regulation and control, according to the difference of rolling speed and reduction of a rough rolling unit, a medium rolling unit and a finishing rolling unit, utilizing microalloy fine-grain strengthening and billet rolling starting temperature to be controlled within the range of 1050 ℃, controlling the rough and medium rolling temperature to be more than 900 ℃, controlling the finishing rolling temperature to be 830-900 ℃, controlling the temperature of water penetration of the finishing rolling billet not to exceed 830 ℃, utilizing the control of a structure strengthening process in the final rolling of an austenite recrystallization zone to carry out quenching, controlling the structural state of deformed austenite, preventing the grains from growing or the carbide from being precipitated to form reticular carbide prematurely, fixing dislocation caused by deformation, increasing the supercooling degree of phase change, and preparing the structure for the transformation of the deformed austenite to ferrite or cementite and pearlite.
Specifically, in the quenching stage, when the finish-rolled steel blank leaves the rolling mill, a cold-hard layer is formed on the surface of the steel bar through intense water cooling, and the cooling speed is higher than the speed of forming martensite so as to obtain coarse martensite; in the tempering stage, heat is transferred from the steel bar core with high temperature to the quenched surface, so that the martensite obtained before is self-tempered, and the tempered martensite formed by self-tempering is utilized to increase the strength and toughness of the steel; after the steel bars are put on a cooling bed, the temperature is controlled between 555-575 ℃, the unconverted austenite of the steel bar core part carries out semi-isothermal phase change, and the alloy elements are uniformly dissolved in the austenite due to high rolling temperature, so that the hardenability is improved. In the aspect of process arrangement, the defects of the traditional process are overcome, the temperature control sections are arranged among all the units, the setting of the recovery sections is not needed, and various control mechanisms can be comprehensively utilized and the requirements of controlled rolling of different specifications and components can be met.
At present, the mechanical property of the steel bar is improved by mainly adding alloy elements in China, and the strength grade of the steel bar is improved by utilizing a solid solution strengthening mechanism, a precipitation strengthening mechanism and a fine grain strengthening mechanism of the alloy elements. During production and smelting, microalloying of vanadium and nitrogen by adding vanadium-nitrogen-gold is a well-known economic and effective method, and simultaneously, the addition of 0.31-0.45% of Cr can improve the hardenability of the steel bar and enhance the phase change and fine grain strengthening effects of the steel bar. In the process of actually producing B600B, V of 0.025-0.045% is added, so that the strengthening effect of vanadium can be fully exerted, and the waste of alloy resources is avoided. The technology adjusts chemical components and rolling technology on the basis of common steel bars, improves the comprehensive performance of the steel bars, and meets various index requirements of B600B high-strength steel bars by adopting controlled rolling and controlled cooling and high-temperature tempering treatment.
A B600B high-strength steel bar comprises the following chemical components in percentage by weight:
c: 0.17-0.22%, Mn: 1.00-1.20%, Si: 0.40-0.55%, V: 0.025-0.045%, P is less than or equal to 0.048%, S is less than or equal to 0.048%, Cr: 0.31-0.45%, and the balance of Fe and inevitable impurities. The carbon equivalent Ceq of the high-strength steel bar is 0.44-0.50%. The mechanical property Re of the high-strength steel bar is 625-780MPa, the yield ratio is not less than 1.08, and Agt is not less than 5.0%.
Table 1 shows the chemical composition of 6 examples, and Table 2 shows the comparison of the mechanical properties of 6 examples. In Table 2, Rm is tensile strength, ReH is upper yield strength, Agt is elongation, and Rm/Re is yield ratio.
Chemical composition of Table 1%
| Serial number | Specification of | C | Si | Mn | V | Cr |
| Example 1 | 25 | 0.21 | 0.45 | 1.06 | 0.025 | 0.34 |
| Example 2 | 25 | 0.21 | 0.46 | 1.06 | 0.035 | 0.34 |
| Example 3 | 25 | 0.21 | 0.44 | 1.07 | 0.045 | 0.34 |
| Example 4 | 25 | 0.21 | 0.45 | 1.05 | 0.025 | 0.31 |
| Example 5 | 25 | 0.21 | 0.44 | 1.05 | 0.026 | 0.36 |
| Example 6 | 25 | 0.21 | 0.46 | 1.06 | 0.026 | 0.45 |
TABLE 2 mechanical Properties
As can be seen from the mechanical properties of Table 2, the V content increased from 0.025% to 0.035%, the average yield strength increased from 667.5MPa to 679.5MPa, an increase of 12 MPa; the V content increased from 0.035% to 0.045%, and the average yield strength increased from 679.5MPa to 686MPa, which increased 6.5 MPa. A small amount of V can fully exert the alloy strengthening effect, and the strength gain is gradually reduced along with the increase of the content, so that the V content is controlled to be 0.025-0.045%, the strengthening effect of vanadium can be fully exerted, and the waste of alloy resources is avoided. The Cr content is increased from 0.31 percent to 0.36 percent, the average yield strength is increased from 661.5MPa to 670.5MPa, and the average yield strength is increased by 9 MPa; the V content is increased from 0.36 percent to 0.40 percent, the average yield strength is increased from 670.5MPa to 681.5MPa, and the average yield strength is increased by 11 MPa. 0.31-0.45% of Cr can fully improve the hardenability of the steel bar, reduce the addition of Si and Mn and reduce the production cost.
As seen from the metallographic diagrams of fig. 1, 2 and 3, the structures of examples 1, 2 and 3 were not significantly different, the edge structure was a tempered martensite structure obtained by self-tempering after high-temperature quenching, the transition region structure was a mixed state of ferrite + pearlite + a small amount of bainite, the ferrite ratio was high, the core structure was pearlite + ferrite + a small amount of bainite, the crystal grains were coarser than the transition region, the pearlite ratio was higher, and the depth of the tempering ring was more than 4.5mm, as shown in table 3.
TABLE 3 metallographic structure
As seen from the metallographic images of fig. 4, 5, and 6, the structures of examples 4, 5, and 6 are not significantly different, and the edge structures are tempered martensite structures obtained by self-tempering after high-temperature quenching, and the core structures are pearlite + ferrite + a very small amount of bainite.
It should be understood that although the present description has been described in terms of various embodiments, not every embodiment includes only a single embodiment, and such description is for clarity purposes only, and those skilled in the art will recognize that the embodiments described herein may be combined as suitable to form other embodiments, as will be appreciated by those skilled in the art.
The above-listed detailed description is only a specific description of a possible embodiment of the present invention, and they are not intended to limit the scope of the present invention, and equivalent embodiments or modifications made without departing from the technical spirit of the present invention should be included in the scope of the present invention.
Claims (8)
1. The B600B high-strength steel bar is characterized in that the high-strength steel bar comprises the following chemical components in percentage by weight:
c: 0.17-0.22%, Mn: 1.00-1.20%, Si: 0.40-0.55%, V: 0.025-0.045%, P is less than or equal to 0.048%, S is less than or equal to 0.048%, Cr: 0.31-0.45%, and the balance of Fe and inevitable impurities.
2. The B600B high-strength steel bar as claimed in claim 1, wherein the carbon equivalent Ceq is 0.44-0.50%.
3. The B600B high-strength steel bar as claimed in claim 1, wherein the mechanical properties Re ═ 625-780MPa, the yield ratio ≥ 1.08, and Agt ≥ 5.0%.
4. The process for producing the B600B high-strength steel bar as claimed in claim 1, wherein the process comprises the following steps:
refining through a refining furnace to obtain refined molten steel;
rolling the refined molten steel through a continuous casting machine to obtain a continuous casting billet;
conveying the continuous casting billet to a steel rolling heating furnace for heating, and then entering a frame roughing mill set for roughing operation to obtain a roughing billet;
after the rough rolling billet is sheared and broken, the rough rolling billet enters a rack middle rolling unit to perform middle rolling operation, and a middle rolling billet is obtained; after the pre-water cooling section of the medium-rolled steel billet is subjected to low-temperature finish rolling, shearing and breaking are carried out, and the medium-rolled steel billet enters a rack finishing mill group to be subjected to finish rolling operation, so that a finish-rolled steel billet is obtained;
carrying out quenching self-tempering treatment on the finish-rolled steel billet;
and cooling and processing the finish rolling billet.
5. The process for producing the B600B high-strength steel bar according to claim 4, wherein the quenching and self-tempering treatment of the finish-rolled steel slab comprises:
the surface of the finish rolling steel billet is rapidly cooled by water through the water, the finish rolling steel billet is used for forming a cold hard layer on the surface of the finish rolling steel billet, and the cooling speed of the surface of the finish rolling steel billet is higher than the speed of forming martensite so as to obtain coarse martensite;
the martensite on the quenching surface of the finish-rolled steel slab is self-tempered by the temperature of the core part of the finish-rolled steel slab, and the strength and toughness of the steel are increased by the tempered martensite formed by the self-tempering.
6. The process for producing the B600B high-strength steel bar as claimed in claim 4, wherein the finish rolled steel slab is cooled by a cooling bed, the temperature of the cooling bed is controlled between 555-575 ℃ to make the non-transformed austenite of the core of the finish rolled steel slab undergo semi-isothermal phase transformation for providing hardenability.
7. The process for producing the B600B high-strength steel bar as claimed in claim 5, wherein the temperature of water passing through the finish rolled steel slab is not more than 830 ℃.
8. The process for producing the B600B high-strength steel bar as claimed in claim 4, wherein the heating temperature of the steel rolling heating furnace is controlled at 1000-1050 ℃; the temperature of the rough rolling operation and the medium rolling operation is more than 900 ℃; the temperature of the finish rolling operation is 830-900 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111101627.2A CN113802066A (en) | 2021-09-18 | 2021-09-18 | B600B high-strength steel bar and production process thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111101627.2A CN113802066A (en) | 2021-09-18 | 2021-09-18 | B600B high-strength steel bar and production process thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN113802066A true CN113802066A (en) | 2021-12-17 |
Family
ID=78895994
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202111101627.2A Pending CN113802066A (en) | 2021-09-18 | 2021-09-18 | B600B high-strength steel bar and production process thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN113802066A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114672732A (en) * | 2022-03-30 | 2022-06-28 | 江苏永钢集团有限公司 | Cr-Ni steel bar and production process thereof |
Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5950116A (en) * | 1982-09-13 | 1984-03-23 | Nakayama Seikosho:Kk | Production of 70kg/mm2 class strong and tough steel bar without hardening and tempering |
| JPH03260010A (en) * | 1990-03-12 | 1991-11-20 | Nippon Steel Corp | Production of non-heattreated steel bar for hot forging and production of hot forged non-heattreated parts |
| CN1730705A (en) * | 2005-08-08 | 2006-02-08 | 宣化钢铁集团有限责任公司 | Microalloyed reinforcing steel bar containing chromium and niobium, and its production process |
| CN101275197A (en) * | 2007-07-19 | 2008-10-01 | 天津钢铁有限公司 | High-strength rebar and manufacturing process thereof |
| CN101445894A (en) * | 2008-11-06 | 2009-06-03 | 天津钢铁有限公司 | Large-specification high-intensity steel rod and production process |
| CN102796970A (en) * | 2012-09-05 | 2012-11-28 | 钢铁研究总院 | Anti-seismic, weather-proof and high-strength YS700MPa hot-rolled reinforced bar |
| CN103911554A (en) * | 2014-04-08 | 2014-07-09 | 张家港联峰钢铁研究所有限公司 | Method for producing level 600MPa fine-grain high-strength aseismic reinforced bars |
| CN106282780A (en) * | 2016-09-29 | 2017-01-04 | 马钢(集团)控股有限公司 | A kind of 630MPa level high-strength hot-rolled steel bar steel and preparation method thereof |
| CN110541113A (en) * | 2019-09-26 | 2019-12-06 | 江苏联峰实业有限公司 | High-strength steel bar and production method thereof |
| CN110565016A (en) * | 2019-09-20 | 2019-12-13 | 江苏联峰实业有限公司 | 630MPa high-strength anti-seismic index reinforcing steel bar and production method thereof |
| CN111004980A (en) * | 2020-01-11 | 2020-04-14 | 武钢集团昆明钢铁股份有限公司 | Preparation method of vanadium-chromium microalloyed large-sized superfine-crystal high-toughness corrosion-resistant anti-seismic reinforcing steel bar |
-
2021
- 2021-09-18 CN CN202111101627.2A patent/CN113802066A/en active Pending
Patent Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5950116A (en) * | 1982-09-13 | 1984-03-23 | Nakayama Seikosho:Kk | Production of 70kg/mm2 class strong and tough steel bar without hardening and tempering |
| JPH03260010A (en) * | 1990-03-12 | 1991-11-20 | Nippon Steel Corp | Production of non-heattreated steel bar for hot forging and production of hot forged non-heattreated parts |
| CN1730705A (en) * | 2005-08-08 | 2006-02-08 | 宣化钢铁集团有限责任公司 | Microalloyed reinforcing steel bar containing chromium and niobium, and its production process |
| CN101275197A (en) * | 2007-07-19 | 2008-10-01 | 天津钢铁有限公司 | High-strength rebar and manufacturing process thereof |
| CN101445894A (en) * | 2008-11-06 | 2009-06-03 | 天津钢铁有限公司 | Large-specification high-intensity steel rod and production process |
| CN102796970A (en) * | 2012-09-05 | 2012-11-28 | 钢铁研究总院 | Anti-seismic, weather-proof and high-strength YS700MPa hot-rolled reinforced bar |
| CN103911554A (en) * | 2014-04-08 | 2014-07-09 | 张家港联峰钢铁研究所有限公司 | Method for producing level 600MPa fine-grain high-strength aseismic reinforced bars |
| CN106282780A (en) * | 2016-09-29 | 2017-01-04 | 马钢(集团)控股有限公司 | A kind of 630MPa level high-strength hot-rolled steel bar steel and preparation method thereof |
| CN110565016A (en) * | 2019-09-20 | 2019-12-13 | 江苏联峰实业有限公司 | 630MPa high-strength anti-seismic index reinforcing steel bar and production method thereof |
| CN110541113A (en) * | 2019-09-26 | 2019-12-06 | 江苏联峰实业有限公司 | High-strength steel bar and production method thereof |
| CN111004980A (en) * | 2020-01-11 | 2020-04-14 | 武钢集团昆明钢铁股份有限公司 | Preparation method of vanadium-chromium microalloyed large-sized superfine-crystal high-toughness corrosion-resistant anti-seismic reinforcing steel bar |
Non-Patent Citations (2)
| Title |
|---|
| 孙庆亮等: "600 MPa级复合微合金化高强钢筋的研制", 《山东冶金》 * |
| 程知松: "《棒线材生产创新工艺及设备》", 31 October 2016, 冶金工业出版社 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114672732A (en) * | 2022-03-30 | 2022-06-28 | 江苏永钢集团有限公司 | Cr-Ni steel bar and production process thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112981235B (en) | Hardened and tempered steel plate with yield strength of 420MPa grade for building structure and production method thereof | |
| EP3715478B1 (en) | Wire rod for cold heading, processed product using same, and manufacturing method therefor | |
| CN101338400B (en) | High strength low-temperature-used low carbon bainite steel and production process thereof | |
| JPH08311551A (en) | Production of high strength seamless steel pipe excellent in sulfide stress cracking resistance | |
| CN111088451A (en) | 600 MPa-level steel bar for reinforced concrete and production method thereof | |
| CN113388779A (en) | 1.5 GPa-grade ultrahigh-strength high-plasticity high-hole-expansion DH steel plate and preparation method thereof | |
| CN106756547A (en) | A kind of yield strength 500MPa grades of cold-rolled steel sheet and preparation method thereof | |
| CN114645201B (en) | High-toughness Q500qNH bridge weather-resistant steel plate and manufacturing method thereof | |
| CN103710635A (en) | 600MPa class chromium/niobium-containing hot-rolled dual-phase steel plate and production method thereof | |
| EP4338862A1 (en) | Method for rolling high-toughness high-strength low-alloy steel | |
| CN107043890A (en) | A kind of 1.5~3.0mm of thickness yield strengths are more than 700MPa Hot Rolling Automobile steel and its manufacture method | |
| CN114000064B (en) | Ultrahigh-strength hot-rolled steel strip with thickness less than 4mm and production method thereof | |
| CN105543666A (en) | Automobile beam steel with 960 MPa yield strength and production method thereof | |
| CN113802066A (en) | B600B high-strength steel bar and production process thereof | |
| KR20120049993A (en) | Method for manufacturing tensile strength 590mpa class hot rolled trip steel with excellent variation of mechanical property | |
| CN105779874B (en) | Cr Nb system 780MPa levels hot-rolled dual-phase steels and its production method | |
| CN102383059A (en) | Hot rolled transformation induced plasticity (TRIP) steel and preparation method thereof | |
| CN111334719A (en) | high-N composite reinforced 500 MPa-grade and 600 MPa-grade steel bar, smelting method and production method | |
| CN111979499A (en) | Production method of low-cost Q460C thick steel plate | |
| CN114875205B (en) | Non-microalloy HRB400E hot rolled ribbed bar and production method thereof | |
| CN114000068B (en) | Low-nitrogen ultrahigh-strength hot-rolled steel strip with thickness of 4-10mm and production method thereof | |
| CN115161440A (en) | Hot-rolled heavy H-shaped steel with yield strength of 560MPa and production method thereof | |
| CN115181887B (en) | 1180 MPa-level low-carbon low-alloy Q & P steel and rapid heat treatment manufacturing method thereof | |
| CN111575583A (en) | High-strength hot-rolled section and temperature and cooling control process thereof | |
| CN113957357A (en) | Hot-rolled wear-resistant steel 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 | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20211217 |