CN111254354B - V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof - Google Patents
V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof Download PDFInfo
- Publication number
- CN111254354B CN111254354B CN202010152284.1A CN202010152284A CN111254354B CN 111254354 B CN111254354 B CN 111254354B CN 202010152284 A CN202010152284 A CN 202010152284A CN 111254354 B CN111254354 B CN 111254354B
- Authority
- CN
- China
- Prior art keywords
- percent
- quenched
- tempered steel
- steel
- forging
- 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
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
- C22C38/02—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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
- C22C38/60—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
- C21D2211/002—Bainite
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 Steel (AREA)
Abstract
The invention discloses V microalloyed high strength and toughness bainite non-quenched and tempered steel, a forging and cooling control process and a production process thereof, wherein the V microalloyed high strength and toughness bainite non-quenched and tempered steel comprises the following chemical components in percentage by weight: 0.20 to 0.30 percent of C, 0.20 to 0.40 percent of Si, 1.90 to 2.10 percent of Mn, less than or equal to 0.010 percent of P, 0.030 to 0.050 percent of S, 0.40 to 0.60 percent of Cr, 0.10 to 0.20 percent of V, 0.015 to 0.025 percent of Ti, less than or equal to 0.20 percent of Ni, less than or equal to 0.20 percent of Mo, 0.020 to 0.045 percent of Al, 60 to 120ppm of N, the balance of Fe and inevitable impurity elements, and the multiplied by N by Ti is less than or equal to 0.00016; compared with 42CrMo quenched and tempered steel, the steel grade has equivalent fatigue performance on the premise of equivalent raw material cost, can omit a heat treatment tempering process for forging enterprises, reduce the manufacturing cost of parts and reduce energy consumption, and can be used for replacing 42CrMo quenched and tempered steel to manufacture parts with higher requirements on strength and toughness.
Description
Technical Field
The invention belongs to the technical field of alloy structural steel, and particularly relates to V microalloyed high-strength and high-toughness bainite non-quenched and tempered steel, and a forging and cooling control process and a production process thereof.
Background
The traditional non-quenched and tempered steel is generally prepared by adding micro V, Nb, Ti and other elements into medium carbon (0.2-0.5% C) steel, performing controlled rolling (forging) and controlled cooling, separating out carbides and nitrides of the V, Nb, Ti and other elements, realizing a strengthening effect, obtaining mechanical properties similar to those of quenching and tempering, and saving the quenching and tempering process. In the cooling process after the deformation, the precipitation strengthening effect of the carbonitride of the element V is the strongest, and the strengthening effect is at a high level and does not change much in a wide temperature range, so in ferrite + pearlite type non-heat-treated steel, composite micro-alloying in which V is added alone or mainly, and Ti and Nb are added simultaneously is often adopted.
However, the ferrite and pearlite type non-quenched and tempered steel has the maximum tensile strength of only 900MPa, and when the strength exceeds the value, the toughness is rapidly reduced, so that the requirement of safety components such as automobile front axles and the like in modern mechanical manufacturing industry on the toughness of steel is difficult to meet. Under certain conditions, bainite can have plasticity and toughness of high-temperature transformation products and strength of low-temperature transformation products, so that bainite type non-quenched and tempered steel is valued by researchers at home and abroad due to good toughness and matching.
The bainite non-quenched and tempered steel obtains higher dislocation density mainly through relatively lower phase transition temperature, so that relatively higher strength is ensured, and meanwhile, certain residual austenite is reserved in the bainite non-quenched and tempered steel, so that the bainite non-quenched and tempered steel obtains relatively higher toughness. Because the phase transformation temperature is low, the diffusion of alloy elements is inhibited in the phase transformation process, so that the carbide of pinning dislocation is difficult to separate out, the movable dislocation density in the bainite non-quenched and tempered steel is high, the yield of the bainite non-quenched and tempered steel is low (less than or equal to 0.70) under the general forging and cooling control process conditions, and the fatigue performance of the bainite non-quenched and tempered steel is reduced.
In order to improve the yield ratio of the bainite non-quenched and tempered steel, many bainite non-quenched and tempered steels are tempered at the temperature of more than 400 ℃, so that on one hand, the tempering process is adopted to improve the process cost, and on the other hand, the bainite non-quenched and tempered steel is low in strength.
Disclosure of Invention
In order to solve the technical problems, the invention provides V microalloyed high-strength and high-toughness bainite non-quenched and tempered steel, and a forging and cooling control process and a production process thereof. Compared with 42CrMo quenched and tempered steel, the steel grade has equivalent fatigue performance on the premise of equivalent raw material cost, can omit a heat treatment tempering process for forging enterprises, reduce the manufacturing cost of parts and reduce energy consumption, and can be used for replacing 42CrMo quenched and tempered steel.
The technical scheme adopted by the invention is as follows:
a V microalloyed high-strength and high-toughness bainite non-quenched and tempered steel comprises the following chemical components in percentage by weight: 0.20 to 0.30 percent of C, 0.20 to 0.40 percent of Si, 1.90 to 2.10 percent of Mn, less than or equal to 0.010 percent of P, 0.030 to 0.050 percent of S, 0.40 to 0.60 percent of Cr, 0.10 to 0.20 percent of V, 0.015 to 0.025 percent of Ti, less than or equal to 0.20 percent of Ni, less than or equal to 0.20 percent of Mo, 0.020 to 0.045 percent of Al, 60 to 120ppm of N, the balance of Fe and inevitable impurity elements, and less than or equal to 0.00016 percent of Ti multiplied by N.
Further, the weight percentage of the V element is preferably 0.10-0.18%.
The weight percentage of the Ni element is preferably 0.04-0.15%.
The weight percentage of the Mo element is preferably 0.04-0.15%.
The tensile strength of the V microalloyed high-strength high-toughness bainite non-quenched and tempered steel is more than or equal to 1030MPa, the yield strength is more than or equal to 770MPa, the elongation after fracture is more than or equal to 16 percent, and the impact energy KU at room temperature2≥60J, a yield ratio of more than or equal to 0.70 and a residual austenite content of 5-12 percent.
The invention also provides a forging-controlling and cooling-controlling process of the V microalloying high-strength and high-toughness bainite non-quenched and tempered steel, wherein a heat-insulating cover is adopted for natural cooling on a cooling-controlling line after the forging is finished, forced air cooling is started when the surface temperature of a part reaches 800 +/-10 ℃, the part is stacked on the cooling-controlling line or enters a slow cooling pit for slow cooling when the surface temperature of the part reaches 400 +/-10 ℃, and the surface temperature of the part is less than or equal to 150 ℃ when the slow cooling is finished.
Further, the forging heating temperature is 1180-1220 ℃, the initial forging temperature is 1100-1150 ℃, and the final forging temperature is 850-900 ℃.
The cooling rate of the strong wind cooling is 0.8 ℃/s-2.4 ℃/s.
The invention also provides a production process of the V microalloyed high-strength and high-toughness bainite non-quenched and tempered steel, which comprises the following steps of: smelting in an electric furnace/converter, and continuously casting after LF refining and RH or VD vacuum degassing
The round billet or the square billet with the side length of 150 mm-450 mm is formed by heating and rolling the continuous casting round billet/square billet
And (3) blanking the round steel, heating the round steel in a medium-frequency induction furnace, and performing controlled forging and cooling by adopting the controlled forging and cooling process.
The invention provides the functions of various element components in V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and the basis that:
c: the element C is necessary for obtaining high strength and hardness. The high C content is advantageous for strength, hardness, etc. of the steel, but is extremely disadvantageous for plasticity and toughness of the steel, and the excessively high C content lowers the transformation temperature of the bainite type non-heat-treated steel, greatly increases the density of mobile dislocations in the steel, lowers the yield ratio, increases the decarburization sensitivity, and deteriorates the fatigue resistance and workability of the steel. Therefore, compared with the traditional ferrite and pearlite non-quenched and tempered steel, the content of C in the steel is properly reduced and is controlled to be below 0.30 percent. However, in order to obtain high strength required for bainite type non-heat-treated steel, the C content should be 0.20% or more, and therefore, the C content is preferably controlled to 0.20 to 0.30%.
Si: si is a main deoxidizing element in steel and has strong solid solution strengthening effect, but the plasticity and toughness of the steel are reduced due to the excessively high content of Si, the activity of C is increased, the decarburization and graphitization tendency of the steel in the heating process of rolling and forging is promoted, smelting is difficult, inclusions are easy to form, and the fatigue resistance of the steel is deteriorated. Therefore, the Si content is controlled to be 0.20-0.40%.
Mn: mn is an effective element for deoxidation and desulfurization, and can promote bainite transformation, and when the content is less than 1.90%, the above-mentioned effect is hardly exerted. However, the content of Mn is too high, which causes the content of residual austenite after phase transformation to be too high, the transformation temperature of bainite to be too low, which causes the yield strength and the yield ratio of steel to be too low, the internal stress to be too large, and the fatigue performance of bainite non-quenched and tempered steel to be deteriorated. Therefore, the content of Mn is controlled to be 1.90-2.10%.
Cr: cr can effectively improve the hardenability of steel and delay bainite transformation so as to obtain required high strength, and can also obviously improve the hardness of bainite ferrite through solid solution strengthening; meanwhile, Cr can also reduce the activity of C, can reduce the decarburization tendency of the surface of steel in the heating, rolling and forging processes, and is beneficial to obtaining high fatigue resistance. However, since too high a content deteriorates the toughness of the steel, the Cr content is controlled to 0.40 to 0.60%.
Ni: ni can improve the hardenability and corrosion resistance of steel and ensure the toughness of the steel at low temperature, but the added Ni element has higher price, which causes higher cost of non-quenched and tempered steel, therefore, the Ni can be properly added when parts are larger, and the content of the added Ni is less than or equal to 0.20 percent.
Mo: mo mainly plays a role in improving hardenability and promoting bainite transformation in steel. Similar to Ni element, Mo element has high price, which results in high cost of non-quenched and tempered steel, therefore, Mo element can be properly added when the parts are large, and the content of added Mo is less than or equal to 0.20 percent.
P: micro segregation is formed when molten steel is solidified, and then the micro segregation is deviated to a grain boundary when the molten steel is heated at a temperature after austenite, so that the brittleness of steel is obviously increased, and the ductility and toughness of the steel are reduced. Therefore, the P content should be controlled to be less than 0.010%.
S: while the formation of MnS inclusions, which are inevitable impurities, and segregation at grain boundaries deteriorate the toughness of steel, thereby reducing the toughness of steel, S forms MnS with Mn, thereby significantly improving the machinability of bainite type non-heat-treated steel. Therefore, the S content should be controlled to be 0.030-0.050%.
V: v and N, C elements in steel form a V (C, N) precipitation phase, so that the precipitation strengthening effect is strong, but because the bainite transformation temperature is low, the diffusion of V is inhibited in the transformation process, so that a large amount of V is dissolved in the steel in a solid solution mode, but because V is a strong carbide forming element, the dissolved V can obviously inhibit the diffusion of C in the bainite transformation process, the bainite ferrite can be refined, the content of V is too high, and the cost is high, so that the content of V is controlled to be 0.10-0.20%.
Ti: ti and N, C elements in steel form Ti (C, N) precipitated phase which has the effect of inhibiting the growth of crystal grains in the heating process, and excessively high Ti content is easy to generate large-grain TiN inclusion by liquation, thereby reducing the fatigue property of the steel and also easily causing the generation of forging cracks, therefore, in order to ensure the crystal grain size of the steel, the Ti content is controlled to be 0.015-0.025 percent.
Al: al is a main deoxidizing element in steel, an AlN precipitated phase is formed with N in the steel, the growth of crystal grains is inhibited, the AlN precipitated phase is insufficient due to too low Al content, the growth of the crystal grains cannot be inhibited, and the purity of the steel is easily reduced due to too high Al content, so that the Al content is controlled to be 0.020-0.045%.
N: as described above, N can combine with V, Ti and Al in the steel to exert grain refining and precipitation strengthening effects, and the above effects are reduced by excessively low N content, but liquating TiN is likely to occur by excessively high N content, and ductility and toughness of the steel are also reduced by solid solution N, so that the N content should be controlled to 60-120ppm and Ti × N is 0.00016 or less.
The ductility and toughness of the steel are improved by properly reducing the content of C on the basis of the components of the traditional ferrite and pearlite type non-quenched and tempered steel, and the granular bainite structure is obtained under the condition of controlled cooling by improving the content of Mn; the method adopts V-N microalloying, and properly adds 0.015-0.025% of trace Ti to refine the size of original austenite grains, avoids TiN liquation by using the Ti multiplied by N of less than or equal to 0.00016, and fully utilizes the function of solid solution V for inhibiting C diffusion in the bainite phase transformation process to refine the sizes of bainite ferrite and M-A islands, thereby ensuring high strength and toughness and high yield ratio.
The relatively high finish forging temperature (900-850 ℃) is adopted in the forging and cooling control process, the high-temperature section after forging is naturally cooled to the surface temperature of the part of 800 ℃ by a heat-preserving cover, and the uniformity of component tissues is ensured, so that the residual austenite in the tissues after phase transformation is uniformly distributed; cooling the medium temperature section (800-400 ℃) by adopting strong wind to ensure that a full-grained bainite structure is obtained; the low-temperature section (400-150 ℃) adopts stacking or is placed in a slow cooling pit for slow cooling, so that the self tempering of the parts is ensured to be sufficient, the movable dislocation density in the bainite is reduced, and the plastic toughness and the yield ratio of the steel are improved.
Compared with the prior art, the V microalloyed bainite non-quenched and tempered steel with high strength and toughness has higher yield ratio and impact toughness, compared with 42CrMo quenched and tempered steel, the V microalloyed bainite non-quenched and tempered steel has equivalent fatigue performance on the premise of equivalent raw material cost, can omit a heat treatment tempering process for forging enterprises, reduce the manufacturing cost of parts and reduce energy consumption, and can be used for replacing 42CrMo quenched and tempered steel to manufacture parts with higher requirements on strength and toughness.
Drawings
FIG. 1 is a structural morphology of a bainite non-quenched and tempered steel in example 1;
FIG. 2 is a microstructure diagram of a bainite non-quenched and tempered steel in example 2;
FIG. 3 is a microstructure diagram of a bainite non-quenched and tempered steel in example 3;
FIG. 4 is a structural morphology diagram of a bainite type non-quenched and tempered steel in comparative example 1;
FIG. 5 is a structural morphology diagram of a bainite type non-quenched and tempered steel in comparative example 2;
FIG. 6 is a structural morphology diagram of a bainite non-quenched and tempered steel in comparative example 3;
FIG. 7 is a structural morphology diagram of 42CrMo quenched and tempered steel.
Detailed Description
The present invention will be described in detail with reference to examples.
In the comparative examples 1 to 3, the steel components in example 1 were used, but the forging and cooling control process of the present invention was not used, and the conventional steel in the following table was 42CrMo quenched and tempered steel.
The chemical compositions in weight percent of the high-toughness bainite non-quenched and tempered steel and the quenched and tempered steel 42CrMo for the front axle of the automobile in the examples 1 to 3 are shown in the table 1, and the steel in the examples 1 to 3 and the conventional steel are smelted by an electric furnace, subjected to LF refining and RH vacuum degassing, and then continuously cast into the steel
The round billet is rolled into by heating
The method comprises the steps of blanking round steel, heating the round steel in a medium-frequency induction furnace, performing roll forging, die forging and trimming on the round steel, and then feeding a controlled cooling line for controlled cooling, namely controlled forging and controlled cooling, wherein a specific controlled forging and controlled cooling process and a traditional steel heat treatment process are shown in a table 2. And (4) taking a standard tensile and impact sample and a metallographic sample on the finished product of the part to perform mechanical property analysis and microstructure analysis.
TABLE 1 chemical composition (wt%) of examples 1-3 and conventional steels
| Examples of the embodiments | C | Si | Mn | P | S | Cr | Ni | Mo | V | Al | Ti | N |
| Example 1 | 0.20 | 0.40 | 2.10 | 0.009 | 0.050 | 0.50 | 0.15 | 0.04 | 0.18 | 0.018 | 0.025 | 0.0060 |
| Example 2 | 0.25 | 0.30 | 2.00 | 0.009 | 0.040 | 0.60 | 0.04 | 0.15 | 0.15 | 0.045 | 0.015 | 0.0100 |
| Example 3 | 0.30 | 0.20 | 1.90 | 0.008 | 0.030 | 0.40 | 0.10 | 0.04 | 0.10 | 0.030 | 0.020 | 0.0075 |
| Conventional steel | 0.42 | 0.25 | 0.70 | 0.012 | 0.002 | 1.13 | 0.04 | 0.20 | 0.04 | 0.025 | 0.006 | 0.0046 |
TABLE 2 summary of the forging and cooling control process, mechanical properties and residual austenite content of the examples, comparative examples and conventional steels
Table 2 summarizes the parameters, mechanical properties and residual austenite content of the forging-controlling and cooling-controlling process of each example, comparative example and conventional steel, and it can be seen that the bainite non-quenched and tempered steel trial-produced by using the steel components and the forging-controlling and cooling-controlling process provided by the invention has the tensile strength of not less than 1030MPa, the yield strength of not less than 770MPa, the elongation after fracture of not less than 16 percent and the room temperature impact power (KU)2) The alloy material has the advantages of more than or equal to 60J, more than or equal to 0.70 of yield ratio, 8-12% of residual austenite content and comprehensive mechanical property meeting the requirement of safety parts. While comparative examples 1-3, which did not employ the controlled forging and cooling process of the present invention, despite the steel composition of the present invention, had significantly lower yield ratios and impact toughness.
The above detailed description of a V microalloyed high toughness bainitic non-quenched and tempered steel and its controlled forging and cooling process and production process with reference to the examples is illustrative and not restrictive, and several examples may be cited within the limits set forth, so that variations and modifications within the spirit and scope of the present invention are deemed to fall within the scope of the present invention.
Claims (8)
1. The V microalloyed high-toughness bainite non-quenched and tempered steel is characterized by comprising the following chemical components in percentage by weight: 0.20 to 0.30 percent of C, 0.20 to 0.40 percent of Si, 1.90 to 2.10 percent of Mn, less than or equal to 0.010 percent of P, 0.030 to 0.050 percent of S, 0.40 to 0.60 percent of Cr, 0.10 to 0.20 percent of V, 0.015 to 0.025 percent of Ti, less than or equal to 0.20 percent of Ni, less than or equal to 0.20 percent of Mo, 0.020 to 0.045 percent of Al, 60 to 120ppm of N, the balance of Fe and inevitable impurity elements, and the multiplied by N by Ti is less than or equal to 0.00016;
the forging and cooling control process of the V microalloyed high-strength high-toughness bainite non-quenched and tempered steel comprises the following steps: and after the forging is finished, naturally cooling the part on a cooling control line by using a heat-insulating cover, starting forced air cooling when the surface temperature of the part reaches 800 +/-10 ℃, stacking the part on the cooling control line or entering a slow cooling pit for slow cooling when the part is cooled to 400 +/-10 ℃, and finishing the slow cooling until the surface temperature of the part is less than or equal to 150 ℃.
2. The V microalloyed high strength and toughness bainite non-quenched and tempered steel as claimed in claim 1, wherein the weight percentage of the V element is 0.10-0.18%.
3. The V microalloyed high strength and toughness bainite non-quenched and tempered steel as claimed in claim 1, wherein the Ni element is preferably 0.04-0.15% by weight.
4. The V microalloyed high strength and toughness bainite non-quenched and tempered steel as claimed in claim 1, wherein the weight percentage of Mo element is 0.04-0.15%.
5. The V microalloyed high strength and toughness bainite non-quenched and tempered steel as claimed in claim 1, wherein the tensile strength of the V microalloyed high strength and toughness bainite non-quenched and tempered steel is not less than 1030MPa, the yield strength is not less than 770MPa, the elongation after fracture is not less than 16%, and the room temperature impact energy KU2The yield ratio is more than or equal to 60J, the yield ratio is more than or equal to 0.70, and the content of residual austenite is 5-12%.
6. The V microalloyed high strength and toughness bainite non-quenched and tempered steel as claimed in claim 1, wherein the forging heating temperature is 1180-1220 ℃, the initial forging temperature is 1100-1150 ℃, and the final forging temperature is 850-900 ℃.
7. The V microalloyed high strength and toughness bainite non-quenched and tempered steel as claimed in claim 1, wherein the cooling rate of the forced air cooling is 0.8-2.4 ℃/s.
8. The process for producing V microalloyed high toughness bainitic non quenched and tempered steel according to any one of claims 1 to 4, characterized by comprising the steps of: smelting in an electric furnace/converter, performing LF refining and RH or VD vacuum degassing, then continuously casting into round billets with phi 300-phi 500mm or square billets with side length of 150 mm-450 mm, rolling the continuously cast round billets/square billets into round steel with phi 40-160 mm through heating, blanking the round steel, heating in a medium-frequency induction furnace, controlling forging and cooling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010152284.1A CN111254354B (en) | 2020-03-06 | 2020-03-06 | V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010152284.1A CN111254354B (en) | 2020-03-06 | 2020-03-06 | V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111254354A CN111254354A (en) | 2020-06-09 |
| CN111254354B true CN111254354B (en) | 2021-11-09 |
Family
ID=70944242
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010152284.1A Active CN111254354B (en) | 2020-03-06 | 2020-03-06 | V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111254354B (en) |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112030069A (en) * | 2020-08-07 | 2020-12-04 | 江苏联峰实业有限公司 | Carbon niobium titanium composite reinforced non-adjustable steel and production method thereof |
| CN112342463B (en) * | 2020-10-12 | 2022-02-01 | 马鞍山钢铁股份有限公司 | high-Ti high-strength high-toughness bainite non-quenched and tempered steel for high-power engine crankshaft and preparation method thereof |
| CN112195412B (en) * | 2020-10-12 | 2021-12-24 | 马鞍山钢铁股份有限公司 | Nb-V microalloyed high-strength high-toughness bainite non-quenched and tempered steel for high-power engine crankshaft and preparation method thereof |
| CN112342462B (en) * | 2020-10-12 | 2022-02-01 | 马鞍山钢铁股份有限公司 | Nb-Ti microalloyed high-strength high-toughness bainite non-quenched and tempered steel for high-power engine crankshaft and preparation method thereof |
| CN112522610B (en) * | 2020-11-18 | 2022-03-25 | 北京交通大学 | V-Ti composite bainite non-quenched and tempered steel structure and manufacturing method thereof |
| CN112410670B (en) * | 2020-11-18 | 2022-02-01 | 北京交通大学 | Bainite/martensite type non-quenched and tempered steel |
| CN112760556A (en) * | 2020-11-30 | 2021-05-07 | 江苏联峰能源装备有限公司 | Preparation method of high-strength and high-toughness bainite non-quenched and tempered steel |
| CN114892079A (en) * | 2022-04-26 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Production method of low-carbon bainite non-quenched and tempered hot-rolled round steel |
| CN115522139B (en) * | 2022-09-02 | 2023-12-08 | 包头钢铁（集团）有限责任公司 | F28MnVRE forgeable non-quenched and tempered hot-rolled round steel for piston and preparation method thereof |
| CN115491605B (en) * | 2022-09-27 | 2023-03-31 | 东风商用车有限公司 | Bainite steel for hot forging, process, device and system for manufacturing hot forged parts |
| CN115896614A (en) * | 2022-10-31 | 2023-04-04 | 中国第一汽车股份有限公司 | Niobium-containing bainite non-quenched and tempered steel material, steering knuckle and preparation method |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0331442A (en) * | 1989-06-29 | 1991-02-12 | Aichi Steel Works Ltd | Tough and hard non-heattreated steel |
| CN101096743A (en) * | 2006-06-27 | 2008-01-02 | 宝山钢铁股份有限公司 | Super-thick non-hardening plastic mold steel and method for manufacturing the same |
| CN101333633A (en) * | 2008-07-30 | 2008-12-31 | 东北大学 | Low carbon bainite type Nb-V composite microalloying non-quenched and tempered steel and method for preparing same |
| CN104220620A (en) * | 2012-03-22 | 2014-12-17 | 新日铁住金株式会社 | Steel material for nitriding, and nitriding component |
| CN104651753A (en) * | 2014-11-28 | 2015-05-27 | 南京钢铁股份有限公司 | Non-quenched and tempered steel for heavy truck balance shaft and manufacturing method thereof |
-
2020
- 2020-03-06 CN CN202010152284.1A patent/CN111254354B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0331442A (en) * | 1989-06-29 | 1991-02-12 | Aichi Steel Works Ltd | Tough and hard non-heattreated steel |
| CN101096743A (en) * | 2006-06-27 | 2008-01-02 | 宝山钢铁股份有限公司 | Super-thick non-hardening plastic mold steel and method for manufacturing the same |
| CN101333633A (en) * | 2008-07-30 | 2008-12-31 | 东北大学 | Low carbon bainite type Nb-V composite microalloying non-quenched and tempered steel and method for preparing same |
| CN104220620A (en) * | 2012-03-22 | 2014-12-17 | 新日铁住金株式会社 | Steel material for nitriding, and nitriding component |
| CN104651753A (en) * | 2014-11-28 | 2015-05-27 | 南京钢铁股份有限公司 | Non-quenched and tempered steel for heavy truck balance shaft and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111254354A (en) | 2020-06-09 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111254354B (en) | V microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof | |
| CN111206191B (en) | Ti-V composite microalloyed superfine bainite non-quenched and tempered steel and forging and cooling control process and production process thereof | |
| CN111549282B (en) | Hot-rolled round steel and preparation method thereof | |
| CN112226691B (en) | Hot rolled steel plate for 1800 MPa-grade hot stamping wheel spoke and manufacturing method thereof | |
| CN104498821B (en) | Medium-manganese high-strength steel for automobiles and production method thereof | |
| CN106319368A (en) | Economical thin chain plate and manufacturing method thereof | |
| CN111118403B (en) | Ti microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof | |
| CN111172466B (en) | Plasticity-enhanced cold-rolled dual-phase steel with tensile strength of 590MPa and production method thereof | |
| CN110578095A (en) | 1200 MPa-level hot-rolled ultrahigh-strength steel plate and manufacturing method thereof | |
| CN112251669B (en) | Hot rolled steel plate for 2000 MPa-level hot stamping wheel spoke and manufacturing method thereof | |
| CN112048677A (en) | Martensite stainless steel for cutter and preparation method thereof | |
| CN112267067B (en) | Hot rolled steel plate for 2000 MPa-level hot stamping wheel rim and manufacturing method thereof | |
| CN111411311A (en) | Steel for die casting corrosion-resistant chain plate and manufacturing method thereof | |
| CN113416902B (en) | Low-cost thermal-forming axle housing steel plate with yield strength of 460MPa and preparation method thereof | |
| CN112226690B (en) | Pickled steel plate for 1800 MPa-level hot stamping wheel rim and manufacturing method thereof | |
| CN107557660A (en) | A kind of 50 DEG C of cryogenic steel of normalizing and its manufacture method | |
| CN112267065B (en) | Pickled steel plate for 2000 MPa-level hot stamping wheel rim and manufacturing method thereof | |
| CN112267066B (en) | Hot rolled steel plate for 1800 MPa-grade hot stamping wheel rim and manufacturing method thereof | |
| CN115627423B (en) | 1600 MPa-grade hot rolled coil and production method thereof | |
| CN105220073A (en) | A kind of blade hot rolled strip and production method and blade treatment process | |
| CN102605249A (en) | Manganese and boron series low-carbon microalloy high-strength non-quenched and tempered steel and production method thereof | |
| CN115572912A (en) | Method for controlling cooling uniformity of steel plate for economic 460 MPa-level engineering structure | |
| CN114774804B (en) | 600 HB-grade hot-rolled low-cost wear-resistant steel plate and manufacturing method thereof | |
| CN116377334B (en) | Ultra-high plastic isotropy 980MPa grade cold-rolled high-strength steel plate and preparation method thereof | |
| CN115386783B (en) | Ultrahigh-strength steel plate with yield strength of 1000MPa and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |