CN105665576B - A kind of steel manufacturing process and its formed parts - Google Patents
A kind of steel manufacturing process and its formed parts Download PDFInfo
- Publication number
- CN105665576B CN105665576B CN201610047076.9A CN201610047076A CN105665576B CN 105665576 B CN105665576 B CN 105665576B CN 201610047076 A CN201610047076 A CN 201610047076A CN 105665576 B CN105665576 B CN 105665576B
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- manufacturing process
- shaping
- twip steel
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 50
- 239000010959 steel Substances 0.000 title claims abstract description 50
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 229910000937 TWIP steel Inorganic materials 0.000 claims abstract description 57
- 238000007493 shaping process Methods 0.000 claims abstract description 24
- 230000003111 delayed effect Effects 0.000 claims abstract description 17
- 238000000034 method Methods 0.000 claims abstract description 14
- 229910001566 austenite Inorganic materials 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 9
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 238000009966 trimming Methods 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 2
- 238000009413 insulation Methods 0.000 claims description 2
- 230000008569 process Effects 0.000 abstract description 10
- 229910000734 martensite Inorganic materials 0.000 abstract description 8
- 230000015572 biosynthetic process Effects 0.000 abstract description 5
- 238000005265 energy consumption Methods 0.000 abstract description 5
- 208000010392 Bone Fractures Diseases 0.000 description 16
- 206010017076 Fracture Diseases 0.000 description 16
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 5
- 229910052739 hydrogen Inorganic materials 0.000 description 5
- 239000001257 hydrogen Substances 0.000 description 5
- 239000011572 manganese Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 239000004411 aluminium Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000007246 mechanism Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 3
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 238000003856 thermoforming Methods 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000012937 correction Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000006356 dehydrogenation reaction Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 208000020442 loss of weight Diseases 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000000116 mitigating effect Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 230000008093 supporting effect Effects 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
Classifications
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—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
Landscapes
- 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 present invention relates to a kind of steel manufacturing process and its formed parts.The steel manufacturing process comprises the following steps：（A）Steel for shaping are provided；（B）By the heat steel to 150 ~ 500 DEG C；（C）Steel after will be heated are sent to steel former；（D）Operation is formed to the steel within the temperature range of 100 ~ 450 DEG C in the steel former.The steel manufacturing process and its formed parts of the present invention can reduce the steel amount of twin that particularly TWIP steel is formed in the forming process even order of magnitude, while suppressing the formation of martensite, so as to provide, a kind of cost is lower and what energy consumption was lower solves the problems, such as the technical scheme of delayed fracture.
Description
Technical field
The present invention relates to a kind of steel manufacturing process and its formed parts.
Background technology
Lightweight and security are the emphasis of auto industry Recent study and development., can be with using the steel plate of high intensity
Under conditions of crashworthiness is not sacrificed, reduce the thickness of steel plate, reach the purpose for mitigating vehicle weight.Meanwhile steel plate
The height of elongation percentage, on the one hand determines whether the steel plate can be shaped as increasingly complex, attractive in appearance and set with optimal engineering
The part shape of meter, on the other hand determining the part of thus steel plate manufacture, there is great energy to inhale when colliding
The ability of receipts.Therefore, high intensity and high-elongation make the important indicator that autobody sheet is developed.
TWIP (Twinning Induced Plasticity, twinning induced plasticity) steel is based on twinning induced plasticity
The high manganese full austenite steel with improving ductile mechanism is need to strengthen, there is high intensity and high elongation percentage, is body of a motor car manufacture
Optional high-quality ferrous materials.It generally has following feature：High Mn content；Microstructure is full austenite；At room temperature
Main Plastic Deformation Mechanism be dislocation motion and twin, phase change induction plasticity effect can also be included（TRIP）.Due to these
Intersecting between tiny deformation twin and dislocation, TWIP steel show strong dynamic Hall-Petch effects, led
Cause high work hardening rate and high tensile strength.Meanwhile high work hardening rate can postpone the generation of localized necking, make
Must deform uniformly to occur, and so as to improve its plastic deformation ability, show high elongation percentage.
However, being also due to the superelevation work hardening capacity that TWIP steel has in itself, the TWIP steel parts after shaping have
Larger internal stress, with reference to itself insuperior hydrogen embrittlement sensitivity resistance, it is hidden after room temperature forming to result in TWIP steel parts
Huge delayed fracture risk is hidden.
Even if starting with from source, strict dehydrogenation is carried out in the manufacturing process of TWIP steel, still can not be ensured
TWIP steel is during auto parts are manufactured into and does not contact hydrogen medium during the military service of TWIP steel parts and hydrogen occurs
Cause delayed fracture.High delayed fracture risk is that TWIP steel can not be in one of major reason of auto industry large-scale application.
The patent documents such as WO2015023012A1, US20080240969A1, CN100577846C in TWIP by adding
Aluminium reduces the risk of hydrogen-induced delayed cracking.However, plus aluminium cause fracture strength（UTS）Reduce so that component process under arms
Middle bearing capacity declines, and causes such plus aluminium TWIP steel loss of weight advantage in body of a motor car application to diminish.Moreover, high aluminium
Addition can make TWIP steel produce the problems such as cast gate blocks in casting process, be unfavorable for continuous casting.
CN104233059A proposes adds Alloying Element Vanadium in TWIP steel, by the use of vanadium carbide particle as hydrogen trap come
Improve the anti-delayed fracture ability of TWIP steel and increase intensity.However, the addition of vanadium will certainly improve the cost of TWIP steel, and
The problem of some solderabilities can be brought.
CN103003002A propose TWIP steel plates are carried out it is preshaped, then by element heats to 500 ~ 700 DEG C, finally
Component is corrected with aligning tool.500 ~ 700 DEG C of heating stepses in this document make the TWIP steel after deformation there occurs
The phenomenon replied or recrystallized, although the residual stress in component can be eliminated comprehensively, solves the problems, such as delayed fracture, this
Method high energy consumption, and two molds are needed to be respectively completed the work of shaping and correction, cost is high, low production efficiency.
The content of the invention
It is an object of the present invention to provide a kind of new steel manufacturing process and its formed parts, it can be with lower
Cost and lower energy consumption solve the problems, such as above-mentioned delayed fracture.The steel manufacturing process and its formed parts of the present invention can drop
The low steel amount of twin that particularly TWIP steel is formed in the forming process even order of magnitude, while suppressing the shape of martensite
Into so as to provide, a kind of cost is lower and what energy consumption was lower solves the problems, such as the technical scheme of delayed fracture.
According to one embodiment of present invention, there is provided a kind of steel manufacturing process, it is characterised in that including following step
Suddenly：（A）Steel for shaping are provided；（B）By the heat steel to 150 ~ 500 DEG C；（C）Steel after will be heated pass
It is sent to steel former；（D）The steel are carried out within the temperature range of 100 ~ 450 DEG C in the steel former
Shaping operation.
According to a preferred embodiment of the present invention, the steel for being used to shape can be twinning induced plasticity steel, institute
State twinning induced plasticity steel may include following component by weight percentage：Mn:12 ~ 30wt%, C:0.4 ~ 1.2wt%, Si:
0 ~ 2 wt%, Al:0 ~ 3wt%, V:The Fe and inevitable impurity of 0 ~ 0.7 wt% and surplus.
According to another preferred embodiment of the invention, in step（B）In, 0.001 ~ 1000 DEG C/s of the rate of heat addition, heating and
It is incubated total time 10s ~ 10h.
According to another preferred embodiment of the invention, the microstructure of the steel after the forming operation includes volume fraction
Austenite more than or equal to 95%.
According to another preferred embodiment of the invention, the 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 are additionally provided, it is characterised in that the formed parts are by this
Any of above-mentioned steel manufacturing process is invented to be made.The formed parts can be used for automobile component, such as B posts reinforcement,
At least one of bumper and door anti-collision joist, wheel spoke.Certainly, the formed parts can be used for other all
Require that the high intensity of lightweight increases the occasion of the component of ductility in terrestrial vehicle.
According to a preferred embodiment of the present invention, the microstructure of the formed parts is more than or equal to including volume fraction
95% austenite.
According to a further advantageous embodiment of the invention, the tensile strength of the formed parts at room temperature is more than
1000MPa.In addition, in the case where shaping degree of deformation is less than or equal to 50% delayed fracture phenomenon does not occur for the formed parts.
Brief description of the drawings
Fig. 1 a are a kind of TWIP steel（Fe-18Mn-0.75C-0.5Si-1.5Al, wt%）Microcosmic group after shaping at room temperature
Knit, produced wherein showing substantial amounts of twin；
Fig. 1 b are microstructure of the TWIP steel the method according to the invention after 300 DEG C of shapings, wherein being displayed without twin
It is brilliant also to be produced without martensite；
Fig. 2 is engineering stress-strain curve of the TWIP steel, wherein stretching when curve above is room temperature is bent
Line, stress strain curve when underlying curve is 300 DEG C, UTS represent tensile strength, and UE represents uniform elongation.
Embodiment
The present inventor it has been investigated that, deformation twin can be formed in TWIP steel deformation processes, some TWIP steel also have Austria
Family name's body phase is changed into martensite, and the delayed fracture that is formed as of the formation of twin or martensite is provided convenience channel, therefore TWIP steel
With so big delayed fracture risk.Therefore, the amount of twin even order of magnitude in forming process in TWIP steel and same is reduced
When suppress martensite be formed as solving the problems, such as that delayed fracture provides a thinking.
The performance and Plastic Deformation Mechanism using austenite as the ferrous materials of matrix such as TWIP steel depends primarily on its fault
Energy（SFE：Stacking Fault Energy）.High manganese TWIP steel stacking fault energies are relatively low at room temperature, can be formed in plastic deformation twin
It is brilliant.And stacking fault energy and temperature are closely related, at a higher temperature, the stacking fault energy of TWIP steel can raise, now its deformation process
In, it is twin to be suppressed or be wholly absent.
Illustrate the manufacturing process and its formed parts of the present invention by taking stamping operation as an example below.There is provided with as follows
The TWIP steel of composition range：Mn:12 ~ 30wt%, C:0.4 ~ 1.2wt%, Si:0 ~ 2 wt%, Al:0 ~ 3wt%, V: 0~0.7
The Fe and inevitable impurity of wt% and surplus, wherein wt% represent matter or percentage by weight.Table 1 is listed used in the present invention
Some typical compositions TWIP steel.Certainly, TWIP steel of the invention is not limited to these compositions, uses other compositions
TWIP steel is also feasible.
These TWIP steel are first heated to 150 ~ 500 DEG C, its rate of heat addition can be 0.001 ~ 1000 DEG C/s, heating and insulation
Total time can be 10s ~ 10h.Then, the TWIP steel after heating is sent to by press by manipulator, rushed at 100 ~ 450 DEG C
Pressing formation.Material after shaping in this way is detected, it is found that delayed fracture phenomenon does not occur in it.
Delayed fracture situation of the TWIP steel of the present invention of table 1 after punching press is heated
。
In addition, also the microstructure of the TWIP steel after normal temperature and 300 DEG C of shapings is contrasted.Fig. 1 a and 1b be
The microstructure comparison diagram of TWIP steel after normal temperature and 300 DEG C of shapings, illustrated in Figure 1 where it can be seen that generated after normal temperature shaping substantial amounts of
Twin, and the austenite crystal for having no twin generation after 300 DEG C of shapings.The volume fraction of austenite can reach 95% with
On.
Fig. 2 shows plastic deformation behavior of the above-mentioned TWIP steel under two reduced temperatures.It can be found that in 300 DEG C of deformations
When, uniform elongation when its 54% uniform elongation and room temperature（56%）About the same, so high ductility can meet absolutely
The stamping needs of most of auto parts.In other words, in 300 DEG C of shapings, although without twin formation, because it is difficult to understand
The deformability splendid at 300 DEG C can also obtain and crystallized ability about the same during room temperature family name's body in itself.Moreover,
During 300 DEG C of deformations, its yield strength and tensile strength are less than situation during deformation at room temperature, in other words, TWIP steel during thermoforming
With lower resistance of deformation, there is positive meaning to the abrasion for reducing press tonnage and reducing diel.
Based on the studies above result, the present invention proposes a kind of for the another of TWIP steel auto parts reduction delayed fracture risk
A kind of logical thinking：TWIP steel is heated in stamping process, makes it at rational temperature（100~450℃）
To suitable stacking fault energy, forming process is relied primarily on dislocation motion and be deformed, control the generation of twin as far as possible.In addition,
TWIP steel deforms in the temperature range will not also occur martensitic traoformation.Due to controlling the formation of twin and martensite, from
And reduce the risk of the part delayed fracture after shaping.
In the present invention, if press temperature is less than 100 DEG C, the stacking fault energy of TWIP steel may not be increased to and be enough
Suppress the degree of twin generation, so being unfavorable for the amount of twin of part after a large amount of reduction shapings；If press temperature is higher than 450
DEG C, it is contemplated that the cooling in from stove to the transfer process of press station, then heating-up temperature may need be higher than 500 DEG C, now
TWIP steel may occur to reply and the phenomenon of partial recrystallisation, causes the yield strength of TWIP steel to decline, influences its military service process
In supporting effect, and heating-up temperature too high the problem of energy consumption being brought too high.
It may also be noted that the TWIP steel of the present invention has at 100 ~ 450 DEG C and the close elongation percentage of room temperature, in room
The lower parts that can be shaped of temperature, can also shape at 100 ~ 450 DEG C.The formed parts formed by the above method can be used for automobile structure
Part, such as at least one of B posts reinforcement, bumper and door anti-collision joist, wheel spoke.Certainly, the formed parts
It can be used in other all terrestrial vehicles requiring that the high intensity of lightweight increases the occasion of the component of ductility.
In addition, the present invention is also equipped with following advantage：
1st, after the heating of TWIP steel strikes out part and is cooled to room temperature, substantial amounts of twin is free of in microstructure, in vapour
Car can be as the TWIP steel of " fresh ", according to TWIP effects, TRIP effects and dislocation mechanism during colliding, there is provided
The farthest ability of deformation and absorption energy.Table 2 illustrate a kind of TWIP steel at 300 DEG C by stretcher strain after obtain
Component at room temperature mechanics performance.From table 2 it can be seen that under different distortion amount the component embody it is very outstanding
Mechanical property, such as at 300 DEG C in the case of stretching 20%, component（Crushed element）Yield strength exceeded 1000MPa,
Tensile strength has reached 1300MPa, and breaking elongation has exceeded 40%, can meet the needs of many automobile applications.
2nd, after the heating of TWIP steel strikes out part and is cooled to room temperature, resilience of the TWIP steel after room temperature shaping can be improved
Problem.
3rd, two curves of comparison diagram 2 are it can be found that the curve of TWIP steel heating stretching has elongation percentage after higher constriction
(post uniform elongation), illustrate that the resistance to crack extension ability of material at this temperature is stronger.By comparison, room
Elongation percentage is very low after the lower shaping TWIP steel constriction of temperature, illustrates there is poor resistance Crack Extension ability, that is, has very high crackle
Sensitiveness.Therefore, it is related to Web edges quality and resistance to crack extension for trimming operation, blanking operation and punch operation etc.
The operation of ability, heating carry out operating the operation being superior at room temperature above.
4th, also need to the occasion of the operations such as reaming and flange for the component after shaping, the component of thermoforming than room temperature into
The component of shape has the ability of more preferable reaming and flange.Such as at 300 DEG C in the case of deformation 20%（Table 2）, component also has
There is elongation percentage after about 10% constriction, and after deforming 20% at room temperature, component only shows elongation percentage after about 4% constriction, constriction
The height of elongation percentage is the key character of reaming and flange ability afterwards.
The machine of the component that the TWIP steel of the present invention of table 2 obtains after according to the deformation of the manufacturing process of the present invention at room temperature
Tool performance
Note：0% a line represents the material property of unstretched deformation in table 2, and 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
This is confined to, steel manufacturing process of the invention may be equally applicable for the operation such as trimming operation, blanking operation and punch operation.
Certainly, based on the teachings of the present invention, those skilled in the art it is also contemplated that some other manufacturing process and formed parts, its
Equally fall within the scope of protection of the present invention.
Claims (8)
1. a kind of steel manufacturing process, it is characterised in that comprise the following steps：
（A）The steel for shaping are provided, the steel for being used to shape are twinning induced plasticity steel, the twin induction modeling
Property steel include following component by weight percentage：Mn:12 ~ 30wt%, C:0.4 ~ 1.2wt%, Si:0 ~ 2 wt%, Al: 0
~ 3wt%, V:The Fe and inevitable impurity of 0 ~ 0.7 wt% and surplus；
（B）By the heat steel to 150 ~ 500 DEG C；
（C）Steel after will be heated are sent to steel former；
（D）Operation is formed to the steel within the temperature range of 100 ~ 450 DEG C in the steel former.
2. steel manufacturing process as claimed in claim 1, it is characterised in that in step（B）In, the rate of heat addition 0.001 ~ 1000
DEG C/s, heating and insulation total time 10s ~ 10h.
3. steel manufacturing process as claimed in claim 1, it is characterised in that the steel are microcosmic after the shaping operation
Tissue includes the austenite that volume fraction is more than or equal to 95%.
4. steel manufacturing process as claimed in claim 1, it is characterised in that the shaping operation include it is stamping operation,
Trimming operation, blanking operation or punch operation.
A kind of 5. formed parts, it is characterised in that the formed parts as the steel any one of claim 1-4 items into
Shape method is made.
6. formed parts as claimed in claim 5, it is characterised in that the microstructure of the formed parts includes volume fraction
Austenite more than or equal to 95%.
7. the formed parts as described in claim 5 or 6, it is characterised in that the tensile strength of the formed parts at room temperature
More than 1000MPa.
8. the formed parts as described in claim 5 or 6, it is characterised in that the formed parts shaping degree of deformation be less than etc.
Delayed fracture does not occur in the case of 50%.
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 |
|---|---|---|---|
| CN201610047076.9A CN105665576B (en) | 2016-01-25 | 2016-01-25 | A kind of steel manufacturing process and its formed parts |
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| Publication Number | Publication Date |
|---|---|
| CN105665576A CN105665576A (en) | 2016-06-15 |
| CN105665576B true CN105665576B (en) | 2018-02-02 |
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ID=56302365
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610047076.9A Active CN105665576B (en) | 2016-01-25 | 2016-01-25 | A kind of steel manufacturing process and its formed parts |
Country Status (2)
| Country | Link |
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| CN (1) | CN105665576B (en) |
| WO (1) | WO2017128478A1 (en) |
Families Citing this family (4)
| 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 high manganese TWIP low temperature resistant steel with high impact toughness and its manufacturing method |
| 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 |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20070018416A (en) * | 2005-08-10 | 2007-02-14 | 현대자동차주식회사 | TSIP-type super high strength steel sheet for automobile body parts and its manufacturing method |
| CN101065503A (en) * | 2004-11-03 | 2007-10-31 | 蒂森克虏伯钢铁股份公司 | High-strength steel strip or sheet exhibiting twip properties and method for producing said strip by direct strip casting |
| CN101235464A (en) * | 2007-11-29 | 2008-08-06 | 北京科技大学 | A copper-nickel alloyed twin-induced plastic steel material and its preparation process |
| CN101422797A (en) * | 2007-10-31 | 2009-05-06 | 中国科学院金属研究所 | Metal sheet forming method |
| WO2009095264A1 (en) * | 2008-01-30 | 2009-08-06 | Corus Staal Bv | Method of producing a hot-rolled twip-steel and a twip-steel product produced thereby |
| CN102400036A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | A twin-induced plasticity steel with high elongation and high hole expansion rate and its manufacturing method |
| CN105200340A (en) * | 2015-09-23 | 2015-12-30 | 宝钢不锈钢有限公司 | 800-1,600 MPa grade high strength austenitic stainless steel, manufacturing method and warm forming method |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1527957B1 (en) * | 1966-04-05 | 1971-11-11 | Hoesch Ag | Process for deep drawing of dethreaded composite sheet |
| JP5396735B2 (en) * | 2008-03-31 | 2014-01-22 | Ｊｆｅスチール株式会社 | High silicon steel strip punching method and punching equipment |
| CN101280352B (en) * | 2008-05-21 | 2010-06-09 | 钢铁研究总院 | Producing method of thermoforming martensitic steel parts |
| CN102989922A (en) * | 2012-12-01 | 2013-03-27 | 西安优耐特容器制造有限公司 | Punch forming method of thin-wall end socket |
| DE102013101276A1 (en) * | 2013-02-08 | 2014-08-14 | Benteler Automobiltechnik Gmbh | Method for producing a motor vehicle stabilizer |
| CN103934360A (en) * | 2014-04-25 | 2014-07-23 | 吉林大学 | Hot stamping and warm blanking composite forming technology and mould for ultrahigh-strength steel |
-
2016
- 2016-01-25 CN CN201610047076.9A patent/CN105665576B/en active Active
- 2016-02-29 WO PCT/CN2016/074804 patent/WO2017128478A1/en active Application Filing
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101065503A (en) * | 2004-11-03 | 2007-10-31 | 蒂森克虏伯钢铁股份公司 | High-strength steel strip or sheet exhibiting twip properties and method for producing said strip by direct strip casting |
| KR20070018416A (en) * | 2005-08-10 | 2007-02-14 | 현대자동차주식회사 | TSIP-type super high strength steel sheet for automobile body parts and its manufacturing method |
| CN101422797A (en) * | 2007-10-31 | 2009-05-06 | 中国科学院金属研究所 | Metal sheet forming method |
| CN101235464A (en) * | 2007-11-29 | 2008-08-06 | 北京科技大学 | A copper-nickel alloyed twin-induced plastic steel material and its preparation process |
| WO2009095264A1 (en) * | 2008-01-30 | 2009-08-06 | Corus Staal Bv | Method of producing a hot-rolled twip-steel and a twip-steel product produced thereby |
| CN102400036A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | A twin-induced plasticity steel with high elongation and high hole expansion rate and its manufacturing method |
| CN105200340A (en) * | 2015-09-23 | 2015-12-30 | 宝钢不锈钢有限公司 | 800-1,600 MPa grade high strength austenitic stainless steel, manufacturing method and warm forming method |
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| WO2017128478A1 (en) | 2017-08-03 |
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