CN105665576A - Steel forming method and forming component - Google Patents
Steel forming method and forming component Download PDFInfo
- Publication number
- CN105665576A CN105665576A CN201610047076.9A CN201610047076A CN105665576A CN 105665576 A CN105665576 A CN 105665576A CN 201610047076 A CN201610047076 A CN 201610047076A CN 105665576 A CN105665576 A CN 105665576A
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- steel
- formed parts
- manufacturing process
- shaping
- twip
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Classifications
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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
- B21D53/00—Making other particular articles
- B21D53/88—Making other particular articles other parts for vehicles, e.g. cowlings, mudguards
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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
- B21D35/00—Combined processes according to or processes combined with methods covered by groups B21D1/00 - B21D31/00
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The invention relates to a steel forming method and forming component. The steel forming method comprises steps as follows: (A) steel for forming is provided; (B) the steel is heated to the temperature of 150-500 DEG C; (C) heated steel is conveyed to steel forming equipment; (D) the steel is formed in the temperature range of 100-450 DEG C in the steel forming equipment. The steel forming method and forming component can reduce the number and even the order of magnitude of twin crystals formed during formation of the steel, particularly TWIP (twinning induced plasticity) steel and can inhibit formation of martensite, so that the technical scheme for solving the delayed cracking problem at the lower cost and under the lower energy consumption is provided.
Description
Technical field
The present invention relates to a kind of steel manufacturing process and formed parts thereof.
Background technology
Lightweight and safety are the emphasis of auto industry Recent study and development. Use the steel plate of high intensity, it is possible to when not sacrificing crashworthiness, reduce the thickness of steel plate, reach to alleviate the purpose of vehicle weight. Simultaneously, the height of the elongation percentage of steel plate, whether determine on the one hand this steel plate to can be shaped as increasingly complex, attractive in appearance and have the part shape of optimum engineering design, another aspect determines the part of thus steel plate manufacture and has the ability of great energy absorption when colliding. Therefore, high intensity and high-elongation make the important indicator that autobody sheet is developed.
TWIP (TwinningInducedPlasticity, twinning induced plasticity) steel is with twinning induced plasticity for main strengthening and the high manganese full austenite steel improving ductile mechanism, there is high intensity and high elongation percentage, be the optional high-quality ferrous materials of body of a motor car manufacture. It is generally of following feature: high Mn content; Microstructure is full austenite; Main Plastic Deformation Mechanism under room temperature is dislocation motion and twin, it is also possible to include phase change induction plasticity effect (TRIP). Intersecting between the deformation twin tiny due to these and dislocation, TWIP steel shows strong dynamic Hall-Petch effect, causes high work hardening rate and high tensile strength. Meanwhile, high work hardening rate can postpone the generation of localized necking so that deformation can uniformly occur, thus improve its plastic deformation ability, shows high elongation percentage.
But, it is also due to the superelevation work hardening capacity that TWIP steel has itself, TWIP steel part after shaping has bigger internal stress, in conjunction with the hydrogen embrittlement sensitivity resistance that itself is insuperior, result in TWIP steel part and conceals huge delayed fracture risk after room temperature forming.
Even if starting with from source, the manufacture process of TWIP steel carrying out strict dehydrogenation, still cannot ensure that TWIP steel does not contact hydrogen medium with in the military service process of TWIP steel part and hydrogen-induced delayed cracking occurs in the process manufacture auto parts. High delayed fracture risk is that TWIP steel can not in one of major reason of auto industry large-scale application.
The patent documentations such as WO2015023012A1, US20080240969A1, CN100577846C reduce the risk of hydrogen-induced delayed cracking by adding aluminum in TWIP.But, add aluminum and cause that fracture strength (UTS) reduces so that in component process under arms, bearing capacity declines, cause that this type of loss of weight advantage in body of a motor car is applied adding aluminum TWIP steel diminishes. And, high aluminum addition can make TWIP steel produce the problems such as cast gate blocking in casting process, is unfavorable for that continuous casting produces.
CN104233059A proposes interpolation Alloying Element Vanadium in TWIP steel, utilizes vanadium carbide particle as hydrogen trap to improve the anti-delayed fracture ability of TWIP steel and to increase intensity. But, the interpolation of vanadium will certainly improve the cost of TWIP steel, and can the band problem of serving solderability.
CN103003002A proposes and carries out preshaped to TWIP steel plate, then by element heats to 500 ~ 700 DEG C, finally with aligning tool, component is corrected. The heating steps of 500 ~ 700 DEG C in this document make deformation after TWIP steel there occurs reply or the phenomenon of recrystallization, although the residual stress that can comprehensively eliminate in component, the problem solving delayed fracture, but the method energy consumption is high, and needing two molds to be respectively completed the work shaping and correcting, cost is high, production efficiency is low.
Summary of the invention
It is an object of the present invention to provide a kind of new steel manufacturing process and formed parts thereof, its problem that can solve above-mentioned delayed fracture with lower cost and less energy consumption. The steel manufacturing process of the present invention and formed parts thereof can reduce the steel amount of twin even order of magnitude that particularly TWIP steel is formed in forming process, and suppress the formation of martensite, thus provide a kind of lower in cost and the less solution delayed fracture problem of energy consumption technical scheme simultaneously.
According to one embodiment of present invention, it is provided that a kind of steel manufacturing process, it is characterised in that comprise the following steps: (A) provides the steel for shaping; (B) by described heat steel to 150 ~ 500 DEG C; (C) steel after being subjected to heating are sent to steel former; (D) in described steel former, in the temperature range of 100 ~ 450 DEG C, described steel are formed operation.
According to a preferred embodiment of the present invention, the described steel for shaping can be twinning induced plasticity steel, described twinning induced plasticity steel can include following component: Mn:12 ~ 30wt% by weight percentage, C:0.4 ~ 1.2wt%, Si:0 ~ 2wt%, the Fe of Al:0 ~ 3wt%, V:0 ~ 0.7wt% and surplus and inevitable impurity.
According to another preferred embodiment of the invention, in step (B), 0.001 ~ 1000 DEG C/s of the rate of heat addition, heats and insulation total time 10s ~ 10h.
According to another preferred embodiment of the invention, described steel microstructure after the forming operation includes the volume fraction austenite be more than or equal to 95%.
According to another preferred embodiment of the invention, described shaping operation can be stamping operation, trimming operation, blanking operation or punch operation.
According to one embodiment of present invention, a kind of formed parts is additionally provided, it is characterised in that this formed parts is made up of any one in the above-mentioned steel manufacturing process of the present invention. Described formed parts can be used for automobile component, for instance at least one in B post reinforcement, bumper and door anti-collision joist, wheel spoke. Certainly, described formed parts can be used for requiring that the high intensity of lightweight increases the occasion of the component of ductility in other all terrestrial vehicles.
According to a preferred embodiment of the present invention, the microstructure of described formed parts includes the volume fraction austenite be more than or equal to 95%.
According to a further advantageous embodiment of the invention, described formed parts tensile strength at room temperature is more than 1000MPa. Additionally, there is not delayed fracture phenomenon when shaping degree of deformation less than or equal to 50% in described formed parts.
Accompanying drawing explanation
Fig. 1 a is the microstructure after a kind of TWIP steel (Fe-18Mn-0.75C-0.5Si-1.5Al, wt%) at room temperature shapes, and wherein shows substantial amounts of twin and produces;
Fig. 1 b is the microstructure after this TWIP steel the method according to the invention shapes at 300 DEG C, is wherein displayed without twin and produces also without martensite;
Fig. 2 is the engineering stress-strain curve of this TWIP steel, and curve wherein above is stress strain curve during room temperature, and the curve being positioned below is stress strain curve when 300 DEG C, and UTS represents tensile strength, and UE represents uniform elongation.
Detailed description of the invention
The present inventor it have been investigated that, TWIP steel deformation process can form deformation twin, some TWIP steel also has austenite phase and becomes martensite, and the delayed fracture that is formed as of the formation of twin or martensite is provided convenience channel, and therefore TWIP steel has so big delayed fracture risk. Therefore, the amount of twin even order of magnitude that reduces in forming process in TWIP steel and simultaneously suppress martensite to be formed as solving delayed fracture problem to provide a thinking.
Performance and the Plastic Deformation Mechanism of the ferrous materials that TWIP steel etc. are matrix with austenite depend primarily on its stacking fault energy (SFE:StackingFaultEnergy). Under room temperature, high manganese TWIP steel stacking fault energy is relatively low, can form twin in plastic deformation. And stacking fault energy is closely related with temperature, at a higher temperature, the stacking fault energy of TWIP steel can raise, and now in its deformation process, twin meeting is suppressed or is wholly absent.
Manufacturing process and the formed parts thereof of the present invention are described for stamping operation below. There is provided the TWIP steel with following composition range: the Fe of Mn:12 ~ 30wt%, C:0.4 ~ 1.2wt%, Si:0 ~ 2wt%, Al:0 ~ 3wt%, V:0 ~ 0.7wt% and surplus and inevitable impurity, wherein wt% represents matter or percentage by weight. Table 1 lists the TWIP steel of some typical compositions used by the present invention. Certainly, the TWIP steel of the present invention is not limited to these compositions, and the TWIP steel using other composition is also feasible.
First heating these TWIP steel to 150 ~ 500 DEG C, its rate of heat addition can be 0.001 ~ 1000 DEG C/s, and heating and insulation total time can be 10s ~ 10h. Then, by mechanical hand, the TWIP steel after heating is sent to press, carries out stamping at 100 ~ 450 DEG C. Material after in this way shaping is detected, it has been found that delayed fracture phenomenon does not all occur for it.
The TWIP steel of table 1 present invention delayed fracture situation after adding drop stamping
。
Additionally, also the microstructure of the TWIP steel after room temperature and 300 DEG C shape has been contrasted. Fig. 1 a and 1b is the microstructure comparison diagram of the TWIP steel after room temperature and 300 DEG C shape, illustrated in Figure 1 where it can be seen that generate substantial amounts of twin after room temperature shapes, and has no, after shaping at 300 DEG C, the austenite crystal that twin generates. Austenitic volume fraction can reach more than 95%.
Fig. 2 illustrates the plastic deformation behavior under two reduced temperatures of the above-mentioned TWIP steel. It appeared that when deforming for 300 DEG C, the uniform elongation (56%) when its uniform elongation of 54% and room temperature is about the same, so high ductility can meet the needs that most auto parts are stamping.In other words, 300 DEG C of shapings, although there is no a twin formation, but due to its austenite this in 300 DEG C time splendid deformability can also obtain with room temperature time crystallized ability about the same. And, when deforming for 300 DEG C, situation when its yield strength and tensile strength are lower than deformation at room temperature, in other words, during thermoforming, TWIP steel has less resistance of deformation, and the abrasion reducing press tonnage and minimizing diel all has the meaning in front.
Based on the studies above result, the present invention proposes a kind of another kind of logical thinking reducing delayed fracture risk for TWIP steel auto parts: TWIP steel is heated in stamping process, its at rational temperature (100 ~ 450 DEG C) are made to obtain suitable stacking fault energy, make forming process rely primarily on dislocation motion to be deformed, control the generation of twin as far as possible. It addition, martensitic phase transformation also will not be there is in this temperature range internal strain in TWIP steel. Owing to controlling the formation of twin and martensite, thus reducing the risk of the part delayed fracture after shaping.
In the present invention, if press temperature is lower than 100 DEG C, then the stacking fault energy of TWIP steel may not be increased to the degree being enough to suppress twin to generate, so the amount of twin of part after being unfavorable for a large amount of reduction shaping; If press temperature is higher than 450 DEG C, consider the cooling from stove to the transfer process of press station, then heating-up temperature is likely to need to be higher than 500 DEG C, now TWIP steel is it may happen that reply the phenomenon with partial recrystallisation, the yield strength causing TWIP steel declines, affect the supporting effect in its military service process, and the too high meeting of heating-up temperature brings the problem that energy consumption is too high.
It may also be noted that the TWIP steel of the present invention has the elongation percentage close with room temperature, the parts that at room temperature can shape at 100 ~ 450 DEG C, also can shape at 100 ~ 450 DEG C. The formed parts formed by said method can be used for automobile component, for instance at least one in B post reinforcement, bumper and door anti-collision joist, wheel spoke. Certainly, described formed parts can be used for requiring that the high intensity of lightweight increases the occasion of the component of ductility in other all terrestrial vehicles.
Additionally, the present invention is also equipped with following advantage:
1, after the heating of TWIP steel strikes out part and is cooled to room temperature, without substantial amounts of twin in microstructure, can as the TWIP steel of " fresh " in the process of collision scenario, according to TWIP effect, TRIP effect and dislocation mechanism, it is provided that the farthest ability of deformation and absorption energy. Table 2 illustrates a kind of TWIP steel at 300 DEG C by the mechanics performance at room temperature of the component that obtains after stretcher strain. As can be seen from Table 2, under different distortion amount, this component all embodies very outstanding mechanical property, such as, when stretching 20% at 300 DEG C, the yield strength of component (crushed element) has exceeded 1000MPa, tensile strength has reached 1300MPa, and breaking elongation has exceeded 40%, it is possible to meet the needs of a lot of automobile application.
2, after the heating of TWIP steel strikes out part and is cooled to room temperature, TWIP steel resilience problem after room temperature shapes can be improved.
3, two curves of comparison diagram 2 have elongation percentage (postuniformelongation) after higher constriction it is found that TWIP steel adds the curve of hot-stretch, and illustrative material resistance to crack extension ability at this temperature is stronger. By comparison, after shaping TWIP steel constriction under room temperature, elongation percentage is very low, illustrates have poor opposing cracks can spread ability, namely has significantly high crack sensitivity.Therefore, trimming operation, blanking operation and punch operation etc. being related to the operation of the ability of Web edges quality and resistance to crack extension, heating carries out the operation that above operation is superior under room temperature.
4, the component after shaping being also needed to the occasion of the operation such as reaming and flange, the component of thermoforming has the ability of better reaming and flange than the component that room temperature shapes. Such as deform when 20% (table 2) at 300 DEG C, component also has elongation percentage after the constriction of about 10%, and deform after 20% under room temperature, component only shows elongation percentage after the constriction of about 4%, and after constriction, the height of elongation percentage is reaming and the key character of flange ability.
The component that the TWIP steel of table 2 present invention obtains after the manufacturing process according to the present invention deforms mechanical performance at room temperature
Note: in table 2,0% a line represents that the material property of unstretched deformation, typical TWIP steel can be (Fe-18Mn-0.75C-0.5Si-1.5Al, wt%).
Although the steel manufacturing process being illustrated above is press-processing method, but the steel manufacturing process of the present invention is not limited thereto, and the steel manufacturing process of the present invention may be equally applicable for the operations such as trimming operation, blanking operation and punch operation. Certainly, based on the teachings of the present invention, those skilled in the art is it is also contemplated that some other manufacturing process and formed parts, and it falls within the scope of protection of the present invention equally.
Claims (9)
1. a steel manufacturing process, it is characterised in that comprise the following steps:
(A) steel for shaping are provided;
(B) by described heat steel to 150 ~ 500 DEG C;
(C) steel after being subjected to heating are sent to steel former;
(D) in described steel former, in the temperature range of 100 ~ 450 DEG C, described steel are formed operation.
2. steel manufacturing process as claimed in claim 1, it is characterized in that, the described steel for shaping are twinning induced plasticity steel, described twinning induced plasticity steel include following component by weight percentage: Mn:12 ~ 30wt%, C:0.4 ~ 1.2wt%, the Fe of Si:0 ~ 2wt%, Al:0 ~ 3wt%, V:0 ~ 0.7wt% and surplus and inevitable impurity.
3. steel manufacturing process as claimed in claim 1 or 2, it is characterised in that in step (B), 0.001 ~ 1000 DEG C/s of the rate of heat addition, heating and insulation total time 10s ~ 10h.
4. steel manufacturing process as claimed in claim 1 or 2, it is characterised in that described steel microstructure after described shaping operation includes the volume fraction austenite be more than or equal to 95%.
5. steel manufacturing process as claimed in claim 1 or 2, it is characterised in that described shaping operation includes stamping operation, trimming operation, blanking operation or punch operation.
6. a formed parts, it is characterised in that described formed parts steel manufacturing process according to any one of claim 1-5 item is made.
7. formed parts as claimed in claim 6, it is characterised in that the microstructure of described formed parts includes the volume fraction austenite be more than or equal to 95%.
8. formed parts as claimed in claims 6 or 7, it is characterised in that described formed parts tensile strength at room temperature is more than 1000MPa.
9. formed parts as claimed in claims 6 or 7, it is characterised in that described formed parts, when shaping degree of deformation less than or equal to 50%, delayed fracture does not occur.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610047076.9A CN105665576B (en) | 2016-01-25 | 2016-01-25 | A kind of steel manufacturing process and its formed parts |
| PCT/CN2016/074804 WO2017128478A1 (en) | 2016-01-25 | 2016-02-29 | Steel forming method and component formed thereby |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
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| CN201610047076.9A CN105665576B (en) | 2016-01-25 | 2016-01-25 | A kind of steel manufacturing process and its formed parts |
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| CN105665576A true CN105665576A (en) | 2016-06-15 |
| CN105665576B CN105665576B (en) | 2018-02-02 |
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| WO (1) | WO2017128478A1 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107574376A (en) * | 2017-09-07 | 2018-01-12 | 北京科技大学 | A kind of high manganese TWIP/TRIP effects symbiosis steel of high strength and low cost plastotype and preparation method thereof |
| CN107760997A (en) * | 2017-09-25 | 2018-03-06 | 武汉钢铁有限公司 | Dual induced plastic high-strength steel and its manufacture method |
| CN108118255A (en) * | 2018-01-08 | 2018-06-05 | 河北工业大学 | A kind of low temperature resistant steel of high manganese TWIP and its manufacturing method with high impact toughness |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102018102974A1 (en) * | 2018-02-09 | 2019-08-14 | Salzgitter Flachstahl Gmbh | A method of manufacturing a component by hot working a manganese steel precursor and a hot worked steel component |
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Also Published As
| Publication number | Publication date |
|---|---|
| CN105665576B (en) | 2018-02-02 |
| WO2017128478A1 (en) | 2017-08-03 |
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