CN114603025A - Selective cooling customized strength hot forming process - Google Patents
Selective cooling customized strength hot forming process Download PDFInfo
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- CN114603025A CN114603025A CN202210502559.9A CN202210502559A CN114603025A CN 114603025 A CN114603025 A CN 114603025A CN 202210502559 A CN202210502559 A CN 202210502559A CN 114603025 A CN114603025 A CN 114603025A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
- B21D22/02—Stamping using rigid devices or tools
- B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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Abstract
The invention relates to a selective cooling customized strength hot forming process which comprises selective slow cooling and selective fast cooling. The soft zone process after the selective slow cooling austenitization is finished comprises the following steps: the area is cooled to the temperature of 300-450 ℃ by adopting the speed of 1-50 ℃/s, then tempered to the temperature of 510-595 ℃, and then integrally quenched and formed to the room temperature, and finally a ferrite + pearlite + a small amount of martensite structure is obtained. The soft zone process after the selective rapid cooling austenitization is finished comprises the following steps: the zone is cooled to the martensite finish transformation temperature of 100-250 ℃ at the speed of 10-100 ℃/s which is greater than the martensite transformation critical temperature, then tempered to 510-595 ℃, and then integrally quenched and formed to the room temperature, and finally the tempered structure is obtained. The invention ensures that the part has multi-performance distribution and simultaneously considers the width of a narrower transition region, can realize the narrower transition region and a smaller performance difference region, does not need to improve the equipment and the process of hot stamping forming and quenching links again, and can be directly applied to the traditional hot stamping equipment and production lines.
Description
Technical Field
The invention relates to the field of hot forming, in particular to a selective cooling customized strength hot forming process.
Background
The hot forming process, a non-isothermal sheet metal forming process combining forming with heat treatment, was first proposed in the last 70 th century, was developed in 1973 by norrbottens jemverk, and was applied in 1975 on wolwo trucks. In 1984, Sabo corporation first used thermoforming technology to make bumper beams in side doors of automobiles, in the last 90 th century, the Reynolds automobiles in France first used thermoforming technology to make bumpers, and the Swedish iron and Steel group made the first thermoformed B-pillar. With the great advantages that thermoformed parts exhibit, the kind and number of thermoformed parts used in automobiles are also increasing.
The hot stamping forming technology for the high-strength steel plate comprises the following main processes: as shown in figure 1, a 0.5-3mm high-strength thin steel plate with a room temperature structure of ferrite and pearlite is heated to 900 ℃ and 950 ℃, the temperature is kept for 3-10 minutes to enable the structure to be fully austenitized, then the steel plate in a red hot state is conveyed into a die with a cooling device through a transfer tool to be subjected to stamping forming, the pressure maintaining effect of the die on the plate can enable the plate to be subjected to temperature reduction quenching treatment at a cooling speed higher than the martensite transformation critical cooling speed (for example, 27 ℃/s of 22MnB 5), in the process, the structure in the steel plate can be completely transformed into a martensite structure from the initial austenite structure, and finally, a high-strength formed part with the strength up to 1500MPa is obtained.
The technical scheme of the prior art I is as follows:
local heating method (local austenitization): according to the requirements of different properties of parts, the zone material requiring martensite is heated to a temperature higher than Ac3, while other zones are kept below Ac3 temperature so as to prevent full austenitization, and the final structure still retains ferrite-pearlite with good toughness. The material above the Ac3 temperature will acquire a fully austenitic phase, after which the material is quenched to obtain martensite.
The first prior art has the following defects:
the local heating method needs to control the heating temperature of different areas in the heating stage, which is usually realized by locally adding heat shielding materials, and the shielding materials need to be removed before the subsequent hot forming process, which increases the complexity and cost of the whole process, and meanwhile, the heat shielding area cannot be miniaturized, otherwise the temperature of the heat shielding area can be influenced by the heat conduction of the surrounding high-temperature area.
The second technical scheme in the prior art:
control of mold temperature method (mold zone quenching): the method has the core that the cooling action of the steel plate is controlled by controlling the temperature difference between the die and the steel plate. The temperature of the die is controlled, so that the heat conduction rate is changed, and more importantly, the cooling degree of the steel plate is limited. If the mold temperature is set to the martensite temperature or higher, the structure finally obtained will not have martensite, and if the mold temperature is further raised to the bainite transformation temperature line or higher, the ferrite-pearlite structure will be finally obtained.
The second prior art has the following defects:
the method for controlling the temperature of the die needs to add a cooling water channel of the die, add a heating wire to control the temperature of the forming die, or change the material and the surface of the die and the like to change the heat transfer performance of the interface. The method of controlling the mold temperature controls the cooling rate of the partial region, so that the dwell cooling time is further prolonged. In addition, the method needs to redesign the mold, so that the manufacturing cost is greatly increased, the performance difference region can not be reduced in size (the mold block with the cooling water channel needs to be provided with the heating wire mold to quickly maintain the air gap), and the width of the transition region is often more than 50 mm.
The third technical scheme in the prior art:
in addition to materials that achieve a gradient profile of properties in a hot forming process such as localized heating and controlled mold temperature, additional localized annealing steps after hot forming, such as localized annealing of additional heat shield materials, or annealing of fully quenched components by selective laser heating, can be used to form soft zones regardless of location and component size.
The third prior art has the following defects:
the same problem exists in the additional local annealing mode of the thermal shielding material as in the first technical scheme, namely, the shielding material needs to be removed after the process is finished, although the selective laser heating method can flexibly control the annealing area, the cost is higher, the additional local annealing method increases the complexity and the production cost of the process, and the batch production cannot be realized. Meanwhile, the additional local annealing is performed after the forming, which can cause the residual stress in an annealing area to be released, generate larger distortion and influence the size precision of the part.
Disclosure of Invention
With the application and popularization of ultra-high strength steel and hot forming technology in engineering, people gradually realize that the load borne by automobile parts in service is not uniformly distributed. From the viewpoint of collision energy distribution, it is not necessarily advantageous to achieve weight reduction and ensure crashworthiness as the strength of the vehicle body member is higher. In order to ensure the integral rigidity and the collision energy absorption effect of the automobile body, the material properties of different parts of the automobile parts are required to be matched with the use requirements. Therefore, designing the gradient performance of the final part according to the distribution form of the load becomes a target pursued by the automobile anti-collision core part.
The hot stamping forming technology can improve the strength of parts and effectively reduce the weight, and is widely applied to the production of automobile parts. Although the conventional hot-stamped parts have high strength and high hardness, the poor plasticity and toughness, and the high strength feature cause difficulties in energy absorption during collision and in reprocessing of the formed parts. In order to solve the problem, the selective rapid cooling customized hot forming process can ensure that the local area of the part obtains better plasticity and toughness, the width of the transition area of the selective slow cooling customized hot forming process is about 30-50mm, the tensile strength of the soft area is 700-2000 MPa, the tensile strength of the hard area is about 1500-2000MPa, and the process is suitable for the area of the soft area larger than 1000mm2And (4) demand. The width of the transition zone of the selective rapid cooling customized hot forming process is about 10-30mm, the tensile strength of the soft zone is 800-. Is suitable for the area of the soft area is less than 1000mm2And (4) demand.
A selective cooling custom strength hot forming process comprising the steps of:
heating the plate to the austenitizing temperature of 900 ℃ and 950 ℃ and preserving the heat for 3-8min to austenitize the structure.
The process of the soft area A after austenitizing is finished comprises the following steps: the area is cooled to the martensite start transformation temperature at the cooling speed of 1-50 ℃/s, the sheet is not formed in the process, only cooling treatment is carried out, and the cooling process can adopt modes of wind, mist, water cooling, flat plate mold contact cooling and the like. Then the temperature is tempered to 510 ℃ and 595 ℃ and the temperature is kept constant for 15 to 60 seconds; finally, the whole is quenched and formed to room temperature, and finally ferrite, pearlite and a small amount of martensite structures are obtained, and the tensile strength of the region is 850-1300 MPa. The hard zone process after austenitizing is finished comprises the following steps: keeping the temperature of the region at 700-850 ℃, then integrally tempering to 750-950 ℃ along with the soft region, and finally integrally quenching and forming to room temperature to obtain a full martensite structure, wherein the tensile strength of the region is 1500-2200 MPa.
The martensite start transformation temperature is 300-450 ℃.
The cooling adopts jet flow cooling, contact type cooling and other modes.
The Vickers hardness of the soft zone is 260-400 HV, and the elongation is 10-25%; the Vickers hardness of the hard zone is 450 and 650 HV.
A selective cooling custom strength hot forming process comprising the steps of:
heating the plate to the austenitizing temperature of 900 ℃ and 950 ℃ and preserving the heat for 3-8min to austenitize the structure.
The soft zone process after austenitizing is finished comprises the following steps: the zone is cooled to the martensite finishing transformation temperature at the cooling speed of 10-100 ℃/s higher than the martensite transformation critical by adopting the modes of jet cooling, contact cooling and the like, and then the tempering is carried out to 510-595 ℃, and the isothermal temperature is kept for 15-60 seconds; finally, the whole is quenched and formed to room temperature, and a tempering structure is finally obtained, wherein the tensile strength of the region is 850-1300 MPa.
The hard zone process after austenitizing is finished comprises the following steps: keeping the temperature of the region at 700-850 ℃, then integrally tempering to 750-950 ℃ along with the soft region, and finally integrally quenching and forming to room temperature to obtain a full martensite structure, wherein the tensile strength of the region is 1500-2200 MPa.
The martensite finish transition temperature is 100-.
The tempered structure is a tempered martensite + tempered sorbite structure.
The cooling adopts jet flow cooling, contact type cooling and other modes.
The Vickers hardness of the soft zone is 260-400 HV, and the elongation is 10-25%; the Vickers hardness of the hard zone is 450 and 650 HV.
The invention has the beneficial effects that: compared with the prior art, the selective slow cooling and fast cooling customized hot forming process adopted by the invention is convenient to operate, does not need to add or remove extra heat shielding materials, and does not influence the austenitizing process flow.
Compared with the prior art, the process has gradient distribution organization before quenching forming, does not need to additionally transform a hot forming die, and reduces the production cost. Meanwhile, the die is a traditional hot forming die, air gaps of the partitioned die are not reserved, the performance difference area can be small in size, and the width of the transition area can reach 10-30 mm. The quenching stage of the selective slow cooling and fast cooling customized hot forming process is the same as that of the traditional hot forming process, the cooling speed of partial area does not need to be controlled, and the pressure maintaining cooling time is prolonged.
Compared with the prior art III, the process does not need an additional annealing procedure after forming, so that the large distortion of parts after forming is avoided. The process adopts jet cooling, contact cooling and other modes, and has low cost and flexible performance difference area setting.
The first cooling section after austenitizing is not formed, and only local cooling treatment is carried out on the plate, and the cooling process can adopt modes of wind, fog, water cooling, flat plate die contact cooling and the like. And after the sheet material is cooled to a proper temperature, the sheet material is moved into a tempering furnace for tempering, and the process not only can ensure that the sheet material has a gradient structure before forming, but also can ensure that each area of the sheet material reaches a high-temperature state, and is convenient for the hot forming process.
The process of the invention adopts a mode of die punch forming and quenching only in the second cooling stage.
The process can enable the parts to have multi-performance distribution while considering the width of the narrower transition region, can realize the narrower transition region and the smaller performance difference region, does not need to improve the equipment and the process of hot stamping forming and quenching links again, and can be directly applied to the traditional hot stamping equipment and production lines.
The selective slow cooling fixed hot forming process does not need to be cooled to a lower temperature during the first cooling, has smaller heat difference between the cooling process and the tempering process, is convenient for the first cooling and tempering operation, saves energy, and can be used for the production of parts in large-range soft areas.
The selective rapid cooling customized hot forming process needs cooling to a lower temperature during the first cooling, and the heat difference between the cooling process and the tempering process is larger, but the cooling speed is required to be high, so that the influence on a high-temperature hard area is smaller, the width of a performance transition area is favorably reduced, and the selective rapid cooling customized hot forming process can be used for the small-range soft area requirement and the production of irregular-shaped soft areas of parts.
The invention adopts jet cooling, contact cooling and other modes to carry out the first cooling operation, and can simultaneously carry out selective slow cooling customized hot forming process and selective fast cooling customized hot forming process in different areas of the same plate material, and the two processes are not influenced mutually. So as to meet the performance requirements of diversified soft zones of parts.
The first cooling section of the selective cooling customized thermoforming process needs shorter cooling time, about 5-20s, and can be used for continuous batch production of roller-bottom and box-type thermoforming production lines.
According to the invention, after the plate is cooled and tempered, the high-temperature slow cooling customized hot forming soft zone ferrite + pearlite structure, the fast cooling customized hot forming soft zone tempered martensite + tempered sorbite structure and the hard zone austenite structure have small difference of rheological stress during high-temperature forming, and the difference is within 100MPa, so that the problems of local deformation and cracking caused by large difference of stress in the forming and quenching processes of different structure properties are avoided.
The selective slow cooling and fast cooling customized hot forming process needs to go through the processes of heating, cooling, reheating and recooling, is beneficial to refining the microstructure, can obtain finer microstructure compared with the prior art II, and is beneficial to improving the comprehensive mechanical property.
Drawings
The invention has the following drawings:
FIG. 1 is a schematic view of a conventional thermoforming process.
FIG. 2 is a schematic view of a selective slow cooling custom thermoforming process of the present invention.
FIG. 3 is a schematic view of the selective rapid cooling custom thermoforming process of the present invention.
FIG. 4 is a scanning electron micrograph of the structure (full martensite) of the conventional hot forming process.
FIG. 5 is a scanning electron microscope image of the soft zone structure (ferrite + pearlite + a small amount of martensite) of the selective slow cooling custom hot forming process of the present invention.
FIG. 6 is a scanning electron microscope image of the soft zone structure (tempered structure) of the selective rapid cooling custom hot forming process of the present invention.
FIG. 7 is a scanning electron micrograph of the hard zone structure (full martensite) of the selectively customized hot forming process of the present invention.
Detailed Description
The present invention will be described in further detail with reference to the accompanying drawings.
The selective cooling customized strength hot forming process is divided into a selective slow cooling customized hot forming process and a selective fast cooling customized hot forming process according to the cooling speed of a selective area after austenitizing.
1. As shown in FIG. 2, the selective slow cooling customized hot forming process requires heating the sheet to austenitizing temperature of 900 ℃ and 950 ℃ and keeping the temperature for 3-8 min.
a. The process of the soft area A after austenitizing is finished comprises the following steps: the region is cooled to the Ms point (about 300-450 ℃) of the martensite start transformation temperature at the cooling speed of 1-50 ℃/s, the sheet is not formed in the process, only cooling treatment is carried out, the cooling process can adopt the modes of wind, mist, water cooling, flat mold contact cooling and the like, the temperature is tempered to below Ac1 temperature (Ac 1 about 700-850 ℃) and is about 510-595 ℃, and the temperature is maintained for 15-60 seconds; in the process, austenite-ferrite-pearlite structure transformation occurs, the whole is quenched and formed to room temperature, a small amount of untransformed austenite generates austenite-martensite structure transformation, and finally ferrite-pearlite-martensite structure is obtained, wherein the tensile strength of the region is about 850-1300 MPa.
b. The hard zone process after austenitizing is finished comprises the following steps: the temperature of the region is kept above Ac1 temperature, about 700-850 ℃, then the soft region is integrally tempered to above Ac3 temperature, about 750-950 ℃, the phase transformation does not occur in the process, the austenite structure is still formed, finally the whole quenching is formed to room temperature, the austenite-martensite structure transformation occurs, and the full-martensite structure is obtained, and the tensile strength of the region is about 1500-2200 MPa.
2. As shown in FIG. 3, the selective rapid cooling and thermal forming process requires heating the sheet to austenitizing temperature of 900-.
a. The soft zone B process after austenitizing is finished comprises the following steps: the region is cooled to the Mf point (about 100 plus 250 ℃) of the martensite finishing transformation temperature at the temperature of 10-100 ℃/s by adopting a cooling speed (for example, the material 22MnB5 is 27 ℃/s, and the material 38MnB5Nb is 12 ℃/s) which is higher than the martensite transformation critical temperature, the austenite-martensite structure transformation is generated in the process, the sheet is not formed in the process, only cooling treatment is carried out, the cooling process can adopt the modes of wind, fog, water cooling, contact cooling of a flat plate mold and the like, and the temperature is tempered to be below Ac1 temperature, about 510 plus 595 ℃, and is kept constant for 15-60 seconds; the transformation from martensite to a tempered structure (tempered martensite/tempered sorbite) occurs in the process, and finally the whole body is quenched and formed to room temperature, and the tempered structure (tempered martensite + tempered sorbite) is finally obtained, and the tensile strength of the region is about 850-. The composition of the tempered structure varies with the tempering temperature, for example, tempered to 550 degrees is largely tempered martensite + a small amount of tempered sorbite.
b. The hard zone process after austenitizing is finished comprises the following steps: the temperature of the region is kept above Ac1 temperature, about 700-850 ℃, then the soft region is integrally tempered to above Ac3 temperature, about 750-950 ℃, the phase transformation does not occur in the process, the austenite structure is still formed, finally the whole quenching is formed to room temperature, the austenite-martensite structure transformation occurs, and the full-martensite structure is obtained, and the tensile strength of the region is about 1500-2200 MPa.
FIG. 4 shows that 38MnB5Nb sample is austenitized at 920 ℃ for 7min and then directly quenched at a cooling rate of 40 ℃/s to obtain a full martensite structure, the structure comprises lath martensite and a small amount of acicular martensite, the tensile strength is 2076MPa, and the elongation is 5.0%.
FIG. 5 shows that after a 38MnB5Nb sample is subjected to austenitizing treatment at 920 ℃ for 7min, the cooled sample is cooled to 450 ℃ at a speed of 25 ℃/s, then the cooled sample is heated to 590 ℃ at a speed of 10 ℃/s, isothermal treatment is carried out for 60 seconds, and finally 70% ferrite + pearlite and 30% martensite structures are obtained through quenching, the tensile strength is 873MPa, and the elongation is 15.3%.
FIG. 6 shows that the tensile strength of a tempered structure (tempered martensite and tempered sorbite) obtained by performing austenitizing treatment on a 38MnB5Nb sample at 920 ℃ for 7min, cooling to 200 ℃ at 40 ℃/s, heating to 550 ℃ at 20 ℃/s, performing isothermal treatment for 15 seconds, and finally quenching is 1105MPa and the elongation of the tempered structure is 11.4%.
FIG. 7 shows that 38MnB5Nb sample is austenitized at 920 ℃ for 7min, then cooled to 750 ℃ at 10 ℃/s, then heated to 850 ℃ at 10 ℃/s, and directly quenched at 40 ℃/s without temperature to obtain a full-martensite structure, wherein the structure is lath martensite and a small amount of needle martensite, the tensile strength of FIG. 7 is 2057MPa, and the elongation is 5.2%.
The above embodiments are merely illustrative, and not restrictive, and those skilled in the relevant art can make various changes and modifications without departing from the spirit and scope of the invention, and therefore all equivalent technical solutions also belong to the scope of the invention.
Those not described in detail in this specification are within the skill of the art.
Claims (9)
1. A selective cooling custom strength hot forming process, comprising the steps of: heating the plate to austenitizing temperature of 900 ℃ and 950 ℃ and preserving heat for 3-8min to austenitize the structure;
the technology of the soft area A after austenitizing is as follows: cooling the soft zone to the martensite start transformation temperature, and keeping the temperature constant for 1-60 seconds; then the temperature is tempered to 510 ℃ and 595 ℃ and the temperature is kept constant for 15 to 60 seconds; finally, the whole is quenched and formed to room temperature, and ferrite, pearlite and a small amount of martensite structures are finally obtained, wherein the tensile strength of a soft zone is 850-1300 MPa; the hard zone process after austenitizing is finished comprises the following steps: keeping the temperature of the hard zone at 700-.
2. The selective cooling custom strength hot forming process of claim 1, wherein: the martensite start transformation temperature is 300-450 ℃.
3. The selective cooling custom strength hot forming process of claim 1, wherein: cooling to the martensite start temperature with a cooling rate of 1-50 ℃/s.
4. The selective cooling custom strength hot forming process of claim 1, wherein: the cooling adopts a jet flow cooling or contact type cooling mode.
5. A selective cooling custom strength hot forming process, comprising the steps of: heating the plate to austenitizing temperature of 900 ℃ and 950 ℃ and preserving heat for 3-8min to austenitize the structure; the soft zone B process after austenitizing is finished comprises the following steps: cooling the soft zone to the martensite finishing transformation temperature at a cooling speed which is higher than the martensite transformation critical temperature, and keeping the temperature for 1-60 seconds; then the temperature is tempered to 510 ℃ and 595 ℃ and the temperature is kept constant for 15 to 60 seconds; finally, integrally quenching and forming to room temperature to finally obtain a tempered structure, wherein the tensile strength of a soft zone is 850-1300 MPa; the hard zone process after austenitizing is finished comprises the following steps: keeping the temperature of the hard zone at 700-.
6. The selective cooling custom strength thermoforming process of claim 5, wherein: the martensite finish transition temperature is 100-.
7. The selective cooling custom strength thermoforming process of claim 5, wherein: the tempered structure is a tempered martensite + tempered sorbite structure.
8. The selective cooling custom strength thermoforming process of claim 5, wherein: the cooling adopts a jet flow cooling or contact type cooling mode.
9. The selective rapid-cool custom strength hot forming process of claim 5, wherein: cooling to the martensite transformation finishing temperature by adopting a cooling speed of 10-100 ℃/s.
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