CN110358967A - Think gauge hot galvanizing Multiphase Steel and its production method - Google Patents
Think gauge hot galvanizing Multiphase Steel and its production method Download PDFInfo
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
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- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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Abstract
The present invention relates to think gauge hot galvanizing Multiphase Steel and its production methods, belong to Multiphase Steel metallurgical technology field.Hot galvanizing complex phase steel chemical composition provided by the invention includes C:0.06~0.13%, Si:0.20~0.50%, Mn:1.50~2.00%, P≤0.025%, S≤0.005%, Mo:0.10~0.60%, Al:0.02~0.08%, Nb:0.010~0.070%, Ti:0.050~0.120%, N≤0.006%, preparation method include smelting, hot rolling, pickling, hot galvanizing annealing operation, and hot galvanizing annealing is using pre-oxidation reducing process.Hot galvanizing Multiphase Steel forming property, welding performance and zinc-plated function admirable prepared by the present invention reach the high-intensitive high requirement extended.
Description
Technical field
The invention belongs to Multiphase Steel metallurgical technology fields, and in particular to think gauge hot galvanizing Multiphase Steel and its production method.
Background technique
With the development of automotive light weight technology technology, automobile steel develops towards high-strength steel direction has become inexorable trend.It is multiple
Phase steel has the characteristics that high-tensile and excellent plasticity, becomes automobile first choice high-strength steel.
Patent (CN109023106A) discloses a kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof, chemical component weight
Amount percentage is respectively as follows: C:0.08~0.12%, Si:0.3~0.6%, Mn:2.0~2.5%, P :≤0.02%, S :≤
0.015%, Al:0.1~0.4%, Cr:0.2~0.5%, Mo:0.1~0.4%, Nb:0.03~0.06%, Ti:0.03~
0.06%, B:0.002~0.003%, surplus are Fe and inevitable impurity.Although passing through its chemical component and preparation method
Hot galvanizing Multiphase Steel is obtained, but its Mn content is higher, and is added to Cr and B, cost and rolling load obviously increase.
Patent (CN108486500A) discloses a kind of cold rolling hot dip galvanizing Multiphase Steel and its production method, chemical component hundred
Divide ratio are as follows: C:0.05~0.13%, Si:0.1~0.5%, Mn:1.5~2.5%, P≤0.015%, S≤0.015%, Al:
0.1~0.6%, Cr:0.2~0.6%, Mo:0.1~0.5%, Nb:0.01~0.06%, Ti:0.01~0.06%, surplus are
Fe and inevitable impurity.Although obtaining hot galvanizing Multiphase Steel by its chemical component and preparation method, which are added
Cr, cost and rolling load obviously increase.
Patent (CN105247089A) discloses a kind of high-strength hot-dip galvanized complex phase steel band production method, chemistry at
Divide percentage are as follows: C:0.13~0.19%, Mn:1.70~2.50%, Si :≤0.15%, Al:0.40~1.00%, Cr:0.05
~0.25%, Nb:0.01~0.05%, P :≤0.10%, Ca :≤0.004%, S :≤0.05%, N :≤0.007%, wherein
0.40% < Al+Si < 1.05% and Mn+Cr > 1.90%, and the steel band has complex phase microscopic structure, and the complex phase is micro-
With volume percentage comprising 8~12% retained austenites, 20~50% bainites, less than 10% martensite, surplus is tissue
Ferrite.Although obtaining hot galvanizing Multiphase Steel by its chemical component and preparation method, C and Mn content is higher, welding
Property reduce.It is added to Cr, cost and rolling load obviously increase.
In conclusion existing invention mainly unilaterally considers the mechanical property of Multiphase Steel, formability is not comprehensively considered
The factors such as energy, zinc-plated performance and welding performance.
Summary of the invention
To solve the above-mentioned problems of the prior art, the present invention provides think gauge hot galvanizing Multiphase Steel, with weight percent
Chemical component than counting the dual phase steel includes C:0.06~0.13%, Si:0.20~0.50%, Mn:1.50~2.00%, P
≤ 0.025%, S≤0.005%, Mo:0.10~0.60%, Al:0.02~0.08%, Nb:0.010~0.070%, Ti:
0.050~0.120%, N≤0.006%, surplus are Fe and inevitable impurity, and surplus is Fe and inevitable impurity.
Preferably, the present invention provides think gauge hot galvanizing Multiphase Steel, the by weight percentage change of the dual phase steel
Study point includes C:0.07~0.12%, Si:0.30~0.50%, Mn:1.60~1.90%, Mo:0.20~0.50%, Al:
0.02~0.07%, Nb:0.020~0.060%, Ti:0.06~0.11%, P≤0.020%, S≤0.005%, N≤
0.006%, surplus is Fe and inevitable impurity.
The present invention also discloses the production methods of high-strength hot-dip zinc-coated Multiphase Steel, comprising the following steps:
(1) it smelting procedure: is smelted according to the chemical component of setting；
(2) slab hot-rolled process: is obtained into hot rolled coil after heating, dephosphorization, hot rolling and section cooling；
(3) acid rolls process；
(4) after hot galvanizing is annealed, required hot galvanizing Multiphase Steel hot galvanizing annealing operation: is made.
Wherein, step (1) smelting procedure is smelted according to the chemical component of above-mentioned high-strength hot-dip zinc-coated Multiphase Steel.
Wherein, step (2) hot-rolled process finish rolling start rolling temperature is 1050~1150 DEG C, and finishing temperature is 860~930 DEG C,
Coiling temperature is 600~650 DEG C.
Wherein, corrosion inhibiter is added in the acid solution that free acid concentration is 80~110g/L and forms acid for step (3) pickling process
Dilution, corrosion inhibiter account for the 0.05~0.10% of pickling solution, and pickling solution is heated to 60~80 DEG C, and pickling time is 25~
50s。
Wherein, step (4) hot galvanizing annealing operation is first heated in oxidation furnace, then in the reduction for having protective atmosphere
Furnace carries out recrystallization annealing, finally enters zinc pot in sealing and carries out hot galvanizing.Further, heating temperature in oxidation furnace
Control is at 720~770 DEG C.
Wherein, protective atmosphere dew-point temperature is -25~-60 DEG C in step (4) hot galvanizing annealing operation furnace.
Wherein, annealing temperature is 780~830 DEG C, is quickly cooled to 440~460 DEG C of temperature of zinc tank furnace nose from annealing temperature,
Its rapid cooling rate CR1 is 50~80 DEG C/s, is cooled to room temperature after zinc-plated with the whole cooling rate rate CR2 of 4~10 DEG C/s.
Beneficial effects of the present invention:
Hot galvanizing Multiphase Steel of the present invention uses low C, Mn to guarantee the superior weldability energy of hot galvanizing Multiphase Steel, addition Nb,
Ti improves its intensity and toughness by crystal grain refinement and precipitation strength, inhibits Carbide Precipitation to make austenite using low cost S i
Sufficiently richness carbon is to improve its intensity；Hot galvanizing annealing of the present invention improves the zinc-plated matter of two-phase steel surface using pre-oxidation reducing process
Amount；The present invention prepares the high-strength Multiphase Steel of think gauge hot galvanizing using hot rolling acid-cleaning plate, thickness can be controlled in what range 2.5~
3.5mm, hot galvanizing Multiphase Steel forming property, welding performance and the zinc-plated function admirable of preparation, yield strength be 707~
715MPa, tensile strength are 920~941MPa, and elongation (A80) is 12.0~12.9%, reach wanting for high-intensitive high extension
It asks, there is significant economic benefit and social benefit.
Specific embodiment
The present invention provides a kind of think gauge hot galvanizing Multiphase Steel, by weight percentage the chemical component packet of the Multiphase Steel
Include C:0.06~0.13%, Si:0.20~0.50%, Mn:1.50~2.00%, P≤0.025%, S≤0.005%, Mo:
0.10~0.60%, Al:0.02~0.08%, Nb:0.010~0.070%, Ti:0.050~0.120%, N≤0.006%,
Surplus is Fe and inevitable impurity.
Preferably, the chemical component of the Multiphase Steel includes C:0.07~0.12% by weight percentage, and Si:0.30~
0.50%, Mn:1.60~1.90%, Mo:0.20~0.50%, Al:0.02~0.07%, Nb:0.020~0.060%, Ti:
0.06~0.11%, P≤0.020%, S≤0.005%, N≤0.006%, surplus are Fe and inevitable impurity.
The mentality of designing of two-phase steel chemical composition of the present invention is as follows:
Carbon: C determines the intensity, plasticity and forming property of steel plate as one of most important component of Multiphase Steel.C is steel
The most apparent element of solid solution strengthening effect in iron material, solid solution C content increases by 0.1% in steel, and about 450MPa can be improved in intensity.
When C content is too low, the stability and martensite hardenability of austenite decline, and lead to low strength, are generally not less than in dual phase steel
0.02%；When C content is excessively high, the plasticity and welding performance of dual phase steel decline, and are generally not more than 0.15% in Multiphase Steel.Therefore,
C content of the present invention is 0.06~0.13%.
Silicon: Si can be solid-solution in the intensity that steel is improved in ferrite and austenite, and effect is only second to C, P, compared with Mn, Cr, Ti
It is strong with the elements such as Ni；Si can also inhibit the precipitation of carbide in ferrite, be enriched with solid solution C atom sufficiently into austenite,
To improve its stability.However, the scale on surface that Si is formed in heating furnace is difficult to remove when Si too high levels, increase
Dephosphorization difficulty is added；SiO2 easily is formed to surface enrichment in annealing process simultaneously, so as to cause surface defects such as plating leakages.Cause
This, Si content of the present invention is 0.20~0.50%.
Manganese: Mn is common solution strengthening element in good deoxidier and desulfurizing agent and steel, in dual phase steel it is general not
Lower than 1.20%.Mn can both form a variety of carbide in conjunction with C and play the role of precipitation strength, and also dissolving in matrix enhances admittedly
Molten strengthening effect.Mn easily forms high melting compound MnS in conjunction with S, to eliminate or weaken hot-short existing due to caused by FeS
As improving the hot-working character of steel.Stabilization of austenite can be improved in Mn, moves to right C curve, to significantly reduce martensite
Critical cooling rate.But when Mn too high levels, to surface enrichment easily in annealing process, a large amount of manganese compounds are formed, so as to cause
The decline of surface galvanizing quality.Therefore, Mn content is 1.50~2.00% in the present invention.
Molybdenum: Mo is similar to Cr effect, hence it is evident that slow pearlite and bainite transformation, to obtain the geneva of high-volume fractional
Body, with proof strength.In addition, Mo oxide Gibbs free energy is suitable with Fe oxide, therefore Mo will not influence the table of dual phase steel
Face galvanizing quality, but its price is costly.Therefore, in the present invention, Mo content is 0.10~0.60%.
Niobium: Nb mainly exists in the form of NbC in Multiphase Steel, the work strengthened with significant crystal grain refinement and intergranular precipitation
With.During hot galvanizing annealing heating, undissolved NbC particle can be with pinning ferrite grain boundaries, to play refinement crystal grain
Effect；When annealing temperature increases to two-phase section, NbC solution temperature is lower, therefore is completely dissolved in matrix, while being dissolved C atom
Into austenite, enrichment is to improve its stability；In cooling procedure, the NbC in ferrite will be precipitated again, to produce bright
Aobvious precipitation strength.Therefore, Nb content is 0.010~0.070%.
Titanium: addition Ti can refine crystal grain, reduce timeliness and cold brittleness.Ti content is too low, and intensity is inadequate, Wu Faman
Sufficient service performance.Ti too high levels can significantly improve intensity, influence service performance, serious to will lead to punching parts cracking.Cause
This, Ti content, which is selected as 0.050%~0.120%, to be advisable.
Aluminium: Al is deoxidier common in steel, while can form AlN pinning crystal boundary, to play the work of refinement crystal grain
With；In addition, Al is similar to Si effect, Carbide Precipitation can be inhibited, to make the sufficiently rich carbon of austenite.Therefore, in the present invention
Al content is 0.02~0.08%.
The present invention also provides the production methods of think gauge hot galvanizing Multiphase Steel, when producing steel plate by block, tool
Body can carry out in accordance with the following steps:
(1) it smelting procedure: is smelted according to above-mentioned designed chemical component, then by being cast as slab；
(2) hot wash process: slab is obtained into hot rolled coil after heating, dephosphorization, hot rolling and section cooling, wherein finish rolling is opened
Rolling temperature is 1050~1100 DEG C, and finishing temperature is 860~930 DEG C, and coiling temperature is 600~650 DEG C；
(3) pickling process: corrosion inhibiter is added in the acid solution that free acid concentration is 80~110g/L and forms pickling solution, delays
Erosion agent accounts for the 0.05~0.10% of pickling solution, pickling solution is heated to 60~80 DEG C, pickling time is 25~50s；
(4) by above-mentioned cold-rolled thin steel strip after hot galvanizing is annealed, required hot galvanizing complex phase hot galvanizing annealing operation: is made
Steel steel plate.Specifically, being made annealing treatment in furnace, is taken out from furnace and be cooled to certain temperature, into the hot galvanizing of zinc pond, wherein
Protective atmosphere dew-point temperature is -25~-60 DEG C in furnace, and annealing temperature is 780~830 DEG C, is quickly cooled to zinc from annealing temperature
440~460 DEG C of tank furnace nose temperature, rapid cooling rate CR1 be 50~80 DEG C/s, it is zinc-plated after with the whole cooling rate rate CR2 of 4~10 DEG C/s
It is cooled to room temperature.Wherein, it is detected by protective atmosphere dew-point temperature in furnace, determines that real gas divides in furnace, to control conjunction
Suitable protective atmosphere (such as hydrogen) content.
Acid solution generally includes at least one of hydrochloric acid, sulfuric acid and nitric acid in pickling process of the present invention, and corrosion inhibiter is hydrochloric acid
Pickling speed can be improved in corrosion inhibiter, pickling process control of the present invention, and pickling is more efficient.
In order to improve complex phase steel surface galvanizing quality, hot galvanizing annealing of the present invention additionally uses pre-oxidation reducing process, has
Body, include oxidation furnace and reduction furnace two parts in line in Continuous Hot Dip Galvanizing Line, strip is first added in oxidation furnace
Heat burns up ROLLING OIL of belt steel surface remaining etc., surface is purified, then by there is the reduction furnace of protective atmosphere to be recrystallized
Annealing finally enters zinc pot in sealing and carries out hot galvanizing.Preferably, heating and temperature control is 720 in oxidation furnace
~770 DEG C.
The thickness of thick rule hot galvanizing Multiphase Steel of the invention can be controlled in any 2.5~3.5mm of range.
The present invention will be further explained and explanation with comparative example by the following examples.
Embodiment 1
The high-strength hot-dip zinc-coated Multiphase Steel of the present embodiment high-mouldability energy is produced by following technique:
(1) smelting procedure: C:0.090%, Si:0.24%, Mn:1.7%, Mo:0.33%, Als:0.045%, Nb:
0.058%, P:0.020%, S:0.005%, N:0.004%, Ti:0.095%, then by being cast as slab, thickness
200mm。
(2) hot-rolled process: obtaining hot rolled coil after heating, dephosphorization, hot rolling and section cooling for slab, wherein heating temperature
Degree is 1240 DEG C, and final rolling temperature is 1080 DEG C, and finishing temperature is 860~900 DEG C, and coiling temperature is 600~630 DEG C, hot rolled plate
Thickness 3.0mm；
(3) pickling process: carrying out pickling for hot rolled plate, and inhibition is added in the acid solution that free acid concentration is 80~110g/L
For dosage form at pickling solution, corrosion inhibiter accounts for the 0.05~0.10% of pickling solution, and 75 DEG C of pickling solution temperature, pickling time 32s；
(4) by above-mentioned hot rolling acid-cleaning plate after hot galvanizing is annealed, required hot galvanizing complex phase hot galvanizing annealing operation: is made
Steel steel plate.750 DEG C are wherein heated in oxidation furnace, protective atmosphere dew-point temperature is -25~-60 DEG C in reduction furnace, annealing temperature
It is 819 DEG C, is quickly cooled to 440~460 DEG C of temperature of zinc tank furnace nose from annealing temperature, rapid cooling rate CR1 is 62 DEG C/s, zinc-plated
It is cooled to room temperature afterwards with the whole cooling rate rate CR2 of 6.0 DEG C/s.
Through detecting, the hot galvanizing Multiphase Steel yield strength 715MPa of the present embodiment, tensile strength 941MPa, elongation
A8012.0%, hot galvanizing Multiphase Steel C, Mn content of the present embodiment is lower, and surface galvanizing quality is good, has good weldability
Can, elongation is high, reaches the high-intensitive high requirement extended.
Embodiment 2
The high-strength hot-dip zinc-coated Multiphase Steel of the present embodiment high-mouldability energy is produced by following technique:
(1) smelting procedure: C:0.090%, Si:0.24%, Mn:1.7%, Mo:0.33%, Als:0.045%, Nb:
0.058%, P:0.020%, S:0.005%, N:0.004%, Ti:0.095%, then by being cast as slab, thickness
200mm。
(2) hot-rolled process: obtaining hot rolled coil after heating, dephosphorization, hot rolling and section cooling for slab, wherein heating temperature
Degree is 1250 DEG C, and final rolling temperature is 1070 DEG C, and finishing temperature is 890~930 DEG C, and coiling temperature is 620~650 DEG C, hot rolled plate
Thickness 3.0mm；
(3) pickling process: carrying out pickling for hot rolled plate, and inhibition is added in the acid solution that free acid concentration is 80~110g/L
For dosage form at pickling solution, corrosion inhibiter accounts for the 0.05~0.10% of pickling solution, pickling solution temperature 70 C, pickling time 35s；
(4) by above-mentioned cold-rolled thin steel strip after hot galvanizing is annealed, required hot galvanizing complex phase hot galvanizing annealing operation: is made
Steel steel plate.740 DEG C are wherein heated in oxidation furnace, protective atmosphere dew-point temperature is -25~-60 DEG C in furnace, annealing temperature 822
DEG C, be quickly cooled to 440~460 DEG C of temperature of zinc tank furnace nose from annealing temperature, rapid cooling rate CR1 is 53 DEG C/s, it is zinc-plated after with
The whole cooling rate rate CR2 of 6.3 DEG C/s is cooled to room temperature.
Through detecting, the hot galvanizing Multiphase Steel yield strength 707MPa of the present embodiment, tensile strength 920MPa, elongation
A8012.9%, hot galvanizing Multiphase Steel C, Mn content of the present embodiment is lower, and surface galvanizing quality is good, has good weldability
Can, elongation is high, reaches the high-intensitive high requirement extended.
The preferred embodiment of the present invention has been described above in detail, still, during present invention is not limited to the embodiments described above
Detail within the scope of the technical concept of the present invention can be with various simple variants of the technical solution of the present invention are made, this
A little simple variants all belong to the scope of protection of the present invention.
It is further to note that specific technical features described in the above specific embodiments, in not lance
In the case where shield, can be combined in any appropriate way, in order to avoid unnecessary repetition, the present invention to it is various can
No further explanation will be given for the combination of energy.
In addition, various embodiments of the present invention can be combined randomly, as long as it is without prejudice to originally
The thought of invention, it should also be regarded as the disclosure of the present invention.
Claims (10)
1. think gauge hot galvanizing Multiphase Steel, it is characterised in that: the chemical component of the Multiphase Steel includes C by weight percentage:
0.06~0.13%, Si:0.20~0.50%, Mn:1.50~2.00%, P≤0.025%, S≤0.005%, Mo:0.10~
0.60%, Al:0.02~0.08%, Nb:0.010~0.070%, Ti:0.050~0.120%, N≤0.006%, surplus are
Fe and inevitable impurity.
2. think gauge hot galvanizing Multiphase Steel according to claim 1, by weight percentage the chemistry of the Multiphase Steel at
Divide includes C:0.07~0.12%, Si:0.30~0.50%, Mn:1.60~1.90%, Mo:0.20~0.50%, Al:0.02
~0.07%, Nb:0.020~0.060%, Ti:0.06~0.11%, P≤0.020%, S≤0.005%, N≤0.006%,
Surplus is Fe and inevitable impurity.
3. the production method of think gauge hot galvanizing Multiphase Steel, it is characterised in that the following steps are included:
(1) it smelting procedure: is smelted to obtain steel billet according to the chemical component of setting；
(2) steel billet hot-rolled process: is obtained into hot rolled coil after heating, dephosphorization, hot rolling and section cooling；
(3) pickling process；
(4) after hot galvanizing is annealed, required hot dip galvanized dual phase steel hot galvanizing annealing operation: is made.
4. the production method of think gauge hot galvanizing Multiphase Steel according to claim 3, it is characterised in that: step (1) is smelted
Process chemical component according to claim 1 or 2 is smelted.
5. the production method of think gauge hot galvanizing Multiphase Steel according to claim 3 or 4, it is characterised in that: step (2) heat
Rolling process finish rolling start rolling temperature is 1050~1150 DEG C, and finishing temperature is 860~930 DEG C, and coiling temperature is 600~650 DEG C.
6. the production method of think gauge hot galvanizing Multiphase Steel according to claim 3, it is characterised in that: step (3) pickling
Corrosion inhibiter is added in the acid solution that free acid concentration is 80~110g/L and forms pickling solution for process, and corrosion inhibiter accounts for pickling solution
0.05~0.10%, pickling solution is heated to 60~80 DEG C, pickling time is 25~50s.
7. the production method of think gauge hot galvanizing Multiphase Steel as claimed in claim 3, it is characterised in that: step (4) hot galvanizing is moved back
Firer's sequence first heats in oxidation furnace, then carries out recrystallization annealing in the reduction furnace for having protective atmosphere, is finally sealing
In the case of enter zinc pot carry out hot galvanizing.
8. the production method of think gauge hot galvanizing Multiphase Steel as claimed in claim 7, it is characterised in that: heating in the oxidation furnace
Temperature is controlled at 720~770 DEG C.
9. the production method of think gauge hot galvanizing Multiphase Steel according to claim 3 or 7, it is characterised in that: step (4) heat
Protective atmosphere dew-point temperature is -25~-60 DEG C in zinc-plated annealing operation furnace.
10. according to the production method of the described in any item think gauge hot galvanizing Multiphase Steels of claim 3~9, it is characterised in that: move back
Fiery temperature is 780~830 DEG C, is quickly cooled to 440~460 DEG C of temperature of zinc tank furnace nose from annealing temperature, rapid cooling rate CR1 is
It 50~80 DEG C/s, is cooled to room temperature after zinc-plated with the whole cooling rate rate CR2 of 4~10 DEG C/s.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112246882A (en) * | 2020-09-29 | 2021-01-22 | 武汉钢铁有限公司 | Method for eliminating hot-dip galvanized transverse stripes of hot-rolled substrate |
| CN112941417A (en) * | 2021-03-03 | 2021-06-11 | 靖江新舟合金材料有限公司 | Alloy coated steel plate and production method thereof |
| CN113355604A (en) * | 2021-06-25 | 2021-09-07 | 攀钢集团攀枝花钢铁研究院有限公司 | Low-cost 700 MPa-grade hot-dip galvanized complex-phase steel plate and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS586926A (en) * | 1981-07-06 | 1983-01-14 | Nippon Kokan Kk <Nkk> | Production of high-toughness high-tensile steel plate |
| CN102758142A (en) * | 2011-04-25 | 2012-10-31 | 宝山钢铁股份有限公司 | Hot-dip galvanized steel sheet with tensile strength higher than 980MPa, and manufacturing method thereof |
| CN105950998A (en) * | 2016-07-11 | 2016-09-21 | 攀钢集团攀枝花钢铁研究院有限公司 | 1000 MPa low-carbon hot-galvanized dual-phase steel and preparation method thereof |
| CN107761006A (en) * | 2017-10-23 | 2018-03-06 | 攀钢集团攀枝花钢铁研究院有限公司 | Strong dual phase steel of low-carbon galvanizing superelevation and preparation method thereof |
-
2019
- 2019-08-21 CN CN201910773962.3A patent/CN110358967A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS586926A (en) * | 1981-07-06 | 1983-01-14 | Nippon Kokan Kk <Nkk> | Production of high-toughness high-tensile steel plate |
| CN102758142A (en) * | 2011-04-25 | 2012-10-31 | 宝山钢铁股份有限公司 | Hot-dip galvanized steel sheet with tensile strength higher than 980MPa, and manufacturing method thereof |
| CN105950998A (en) * | 2016-07-11 | 2016-09-21 | 攀钢集团攀枝花钢铁研究院有限公司 | 1000 MPa low-carbon hot-galvanized dual-phase steel and preparation method thereof |
| CN107761006A (en) * | 2017-10-23 | 2018-03-06 | 攀钢集团攀枝花钢铁研究院有限公司 | Strong dual phase steel of low-carbon galvanizing superelevation and preparation method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112246882A (en) * | 2020-09-29 | 2021-01-22 | 武汉钢铁有限公司 | Method for eliminating hot-dip galvanized transverse stripes of hot-rolled substrate |
| CN112941417A (en) * | 2021-03-03 | 2021-06-11 | 靖江新舟合金材料有限公司 | Alloy coated steel plate and production method thereof |
| CN113355604A (en) * | 2021-06-25 | 2021-09-07 | 攀钢集团攀枝花钢铁研究院有限公司 | Low-cost 700 MPa-grade hot-dip galvanized complex-phase steel plate and preparation method thereof |
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