CN108624818A - 400-500MPa grades high uniform elongation hot continuous-milling steel plate and its manufacturing method - Google Patents
400-500MPa grades high uniform elongation hot continuous-milling steel plate and its manufacturing method Download PDFInfo
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- CN108624818A CN108624818A CN201710183338.9A CN201710183338A CN108624818A CN 108624818 A CN108624818 A CN 108624818A CN 201710183338 A CN201710183338 A CN 201710183338A CN 108624818 A CN108624818 A CN 108624818A
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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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/06—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
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- 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
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
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- Organic Chemistry (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
400 500MPa grades high uniform elongation hot continuous-milling steel plate and its manufacturing method, composition by weight percent are：C 0.04~0.08%, Si 0~1.6%, Mn 0.8~1.5%, P≤0.035%, S≤0.001%, Al 0.025~0.060%, more than one element in N≤0.0060% and Ti≤0.03%, Nb≤0.05% and Ca≤0.0050%, remaining is Fe and inevitable impurity.Steel plate of the present invention is not required to through Overheating Treatment, conventional hot rolling line directly produces, Thin Specs (≤12mm), tensile strength are 400MPa or more ranks, uniform elongation is 20% or more high uniform elongation；Hot rolling postcooling technique has good cold-workability and welding performance compared with simple, performance is uniform, plate shape is good, and production cost is low, disclosure satisfy that the forming property requirement of the complex-shaped parts such as automobile chassis and structural member.
Description
Technical field
The invention belongs to metal material field more particularly to a kind of 400-500MPa grades high uniform elongation hot continuous-milling steel plates
And its manufacturing method, it is 400-500MPa grades not have to heat treatment, product thickness no more than 12mm, intensity, high uniform elongation,
This steel plate is be especially suitable for passenger-car chassis component.
Background technology
Steel plate is one of most common material on automobile, it is widely used in the structural member of manufacture automobile, and it is each to undertake automobile
The different load of position.
Hot rolled steel plate is mainly used for passenger-car chassis, wheel, suspension and its peripheral parts, its weight accounts about car body gross weight
25% or more of amount.400-500MPa grades of hot rolled steel plate is the material for the strength range being most widely used, it usually has
Very good forming property and welding performance, can meet the forming requirements of most auto parts and components.But with automobile
Upper attendant equipment is continuously increased, and the shape of many parts also becomes to become increasingly complex, and the requirement to steel formability performance also becomes
It obtains higher and higher.Accordingly, it is desirable to be able to obtain the material with more preferable forming property, the contradiction faced is solved.
When using traditional steel plate, their yield strength, tensile strength and extension are usually only focused on
Rate.But this is far from being enough in finer processing technology.The steel plate for obtaining higher forming property is not to carry
High fracture elongation can.In fact, for process for stamping and forming, the raising of uniform elongation, which has, more importantly to be made
With.In general, the fracture elongation of steel plate is improved, so that it may to improve the uniform elongation of steel plate.But it is higher to meet
When forming requirements and the fracture elongation for improving steel plate become increasingly difficult, the uniform elongation of steel plate is individually improved, is become more
Exacerbation is wanted.And in fact, by the adjustment to steel plate ingredient, microstructure, technique, it can make some steel plates that need not improve
Fracture elongation, it will be able to improve uniform elongation, improve the stamping formabilily of steel plate.
Canadian Patent CA2775031 propose an ingredient be 0.06%-0.12%C, 0.01%-1.0%Si,
1.2%-3.0%Mn ,≤0.015% Ρ ,≤0.005%S ,≤0.08%Al, 0.005%-0.07%Nb, 0.005%-
0.025%Ti ,≤0.010% Ν and≤0.005%O, remaining is the thick specification hot-rolled manufacturing process of Fe or impurity,
After 1000-1300 DEG C of heating, finishing temperature is not less than Ar3, and ensures that the rolling at≤900 DEG C is thinned and be not less than 50%, with
It is cooled to 500-680 DEG C with the speed of >=5 DEG C/s afterwards, 550-700 DEG C is being heated to the speed of 2 DEG C/s or more, is then accelerated
It is cooling.The accounting of the two-phase structure for being organized as bainite+Ma-Austria island formed, wherein Ma-Austria island is 3-20%.
Japanese invention JP2010063547 uses following component：0.03-0.20%C, 0.05-0.6%Si, 0.3-2.0%
Mn ,≤0.015% Ρ ,≤0.003%S ,≤0.05%Al ,≤0.010% Ν, in order to improve intensity can add Cr, Ni,
Mo, Cu, Nb, Ti, V, remaining is Fe or impurity, carbon equivalent 0.33-0.50%.In >=850 DEG C of finish to gauges, with cooling velocity≤1.0
DEG C/s is cooled to α-γ two-phase sections (580-650 DEG C), it keeps accelerating cooling, cooling velocity≤100 DEG C/s after twenty minutes.Composition group
It is woven to 10-45% ferrites and upper bainite, martensite content≤5% in upper bainite.Manufacture tensile strength >=590MPa, tool
It is >=the steel plate of 12mm to have low yield strength ratio, high uniform elongation, thickness.
Invention content
The purpose of the present invention is to provide a kind of 400-500MPa grades high uniform elongation hot continuous-milling steel plate and its manufacturers
Method, the steel plate are not required to through Overheating Treatment, conventional hot rolling line directly produces, Thin Specs (≤12mm), tensile strength are
400MPa or more ranks, the high uniform elongation that uniform elongation is 20% or more；After this high uniform elongation hot-rolled steel plate
Cooling technique has good cold-workability and welding performance, production cost is low, disclosure satisfy that compared with simple, performance is uniform, plate shape is good
The forming property requirement of the complex-shaped parts such as automobile chassis and structural member.The hot-rolled product is after pickling, surface quality meeting
Having significantly improves.
In order to achieve the above objectives, the technical scheme is that：
400-500MPa grades high uniform elongation hot continuous-milling steel plate, composition by weight percent are：C 0.04~0.08%,
Si 0~1.6%, Mn 0.8~1.5%, P≤0.035%, S≤0.001%, Al 0.025~0.060%, N≤
0.0060% and Ti≤0.03%, Nb≤0.05% and Ca≤0.0050% in more than one element, remaining is Fe and can not to keep away
The impurity exempted from.
Preferably, the microstructure of steel plate is the bainite of 10-30% and the ferrite of 70-90%, wherein length-width ratio
Ferritic ratio 1.0~1.2 is not less than 80%.
Preferably, steel plate yield strength >=460MPa, tensile strength >=550MPa, uniform elongation are 20% or more, -40
DEG C Charpy-V impact power (single value) >=100J, Kca (- 10 ° DEG C) >=6500N/mm1.5。
Preferably, steel plate thickness≤12mm.
Each alloys producing in the present invention：
C：It is used to form phase carbide reinforced enough, to ensure that the intensity rank of steel, C too low-intensity do not reach requirement, C is too
Height is unfavorable to welding performance and forming property.
Si：Effect in steel has following three：
1. solution strengthening effect improves the intensity of steel；
2. can play a part of to accelerate to ferritic transformation to austenite, austenite is made to add to ferritic rate of transformation
Soon；
3. preventing the precipitation of C compounds, the appearance of pearlite phase is avoided.
But too high Si contents are easy that surface of steel plate is made to generate the surface defects such as red iron sheet.
Mn：It is solution strengthening element, insufficient less than the intensity of 1.0% steel, the too high plasticity that can make steel declines.
P：It is the impurity element in steel, the lower content should be the better.
S：It is also the impurity element in steel, usually requires that in steel S contents 0.01% hereinafter, but in order to ensure that hot rolling is high-strength
Spending steel plate has higher hole expansibility, it is desirable that the content of S must be below 0.001%.
Al：The deoxidant element in steel, reduce steel in oxide be mingled with, pure steel, be conducive to improve steel plate at
Shape performance.
Ti：It is effective crystal grain thinning, improves the element of intensity and toughness, is present in the form of carbide and carbonitride
In steel, it is small that addition strengthens effect less than 0.01%.
Nb：It is effective crystal grain thinning, improves the element of intensity and toughness, is present in the form of carbide and carbonitride
In steel.The recrystallization temperature of steel can also be reduced.
Ca：The form of sulfide, improves the plasticity and toughness of steel plate, helps to improve the reaming of steel plate in changeable steel
Rate.
The microstructure of steel plate of the present invention is the bainite of 10-30% and the ferrite of 70-90%, wherein length-width ratio
Ferritic ratio 1.0~1.2 is not less than 80%.
Ferrite has good ductility, can provide material higher uniform elongation.Ferrite can also expand
The extension of bainite plastic deformation；And ensure that most of ferritic length-width ratios 1.0~1.2, can make ferritic
Deformation is more uniform, it is advantageously ensured that material has higher uniform elongation.
Bainite has higher intensity, can improve the integral strength of material.
The raising of the uniform extension property of material is because the soft phase of ferrite between the hard phase of bainite has played whole association
It adjusts caused by denaturation.There is the process for having slowed down bainite and stress concentration occurring due to ferritic, improves the uniform of material
Elongation percentage.
The manufacturing method of the high uniform elongation hot continuous-milling steel plate of 400-500MPa grades of the present invention comprising following steps：
1) it smelts, cast
It smelted by mentioned component, be cast as base；
2) heating of plate blank, heating and temperature control is at 1150~1250 DEG C；
3) it rolls, is rolled at a temperature of not less than Ar3, rolling reduction 80-95%, finishing temperature 800~900
℃；
4) steel plate after finish to gauge is as cold as 600~750 DEG C with the cooling velocity of 50~150 DEG C/s, then with 3~10 DEG C/s's
Cooling velocity cools down 2~10 seconds in air, is then cooled to 350~500 DEG C again with the cooling velocity of 100 DEG C/s or more
And batch, then it is air-cooled to room temperature.
The explanation of process conditions in the present invention：
Heating temperature is less than 1150 DEG C, and microalloy element dissolving is insufficient, fails the effect for making full use of microalloy element,
Strength reduction.Higher than 1250 DEG C crystal grain are easy roughening, unfavorable to improving steel plate toughness.
In austenite, crystal boundary area carries out roughing to slab again, passes through the recrystallization softening austenite grain after rolling deformation, steel
The deflection of plate passes through austenite low-temperature space in 80-95%, finishing temperature control in 780~850 DEG C of austenite Unhydrated cement
Rolling deformation, so that austenite crystal intragranular is formed Zona transformans and because of the carbonitride precipitates of strain-induced microalloy element, refinement
The phase-change product of austenite improves the toughness of steel plate.
Steel plate is cooled to 600~750 DEG C with 50~150 DEG C/s or more cooling velocities after finish to gauge, in air with 3~10
DEG C/cooling velocity of s cools down 2~10 seconds, so that partial austenitic is transformed into ferrite in this temperature range, subsequent steel plate is with 100
DEG C/cooling velocity of s or more is cooled to 350~500 DEG C and batches, so that material is entered Bainite Region, ultimately forms about 10-30%
Bainite and about 70-90% ferrite.In order to ensure that material uniform elongation has 3 percentage points or more of raising,
It asks length-width ratio in microstructure to be not less than 80% in 1.0~1.2 ferritic ratio, sees Fig. 1.If coiling temperature is higher than 500
DEG C, it is susceptible to a large amount of pearlite (more than 20%) in steel plate microstructure, the uniform elongation of steel plate can be made to reduce.
As automobile chassis and structural member material, traditional solution is strengthened and precipitation strength steel plate must have enough intensity
With higher fracture elongation, but fracture elongation improve it is relatively difficult, and under conditions of identical fracture elongation, by changing
The microstructure become inside steel plate is constituted, and is improved the uniform elongation of steel plate, equally be can effectively improve the formability of steel plate
Can, it reduces and even avoids generating cracking phenomena in the forming of Irregular Shaped Parts.
The present invention is a kind of cooling technique without by segmentation after modifier treatment, hot rolling, makes equality strength level steel plate
On uniform elongation obtain at least three percentage point raising hot rolled steel plate and its manufacturing method, such shape steel plate have compared with
High uniform elongation and good forming property are mainly used for the more complex shaped components forming such as automobile chassis and wheel and add
Work.
There are prodigious difference compared with existing patent by the present invention：
1, intensity：The strength range that the present invention is applicable in is wider, can be down to 400MPa.Japan Patent JP2010063547, add
Strength range applicable patent of putting on airs CA2775031 is in 517MPa or more.
2, thickness：Thickness≤12mm of the present invention is suitable for relatively thin thickness.Japan Patent JP2010063547, Canada
The thickness of patent CA2775031 is then in 14mm or more.
3, it organizes：The present invention is organized as ferrite+10-30% bainites.And Canadian Patent CA2775031 is organized as
Bainite+3-20% martensites and Japan Patent JP2010063547's is organized as 10-45% ferrites+bainite (≤5% horse
Family name's body).
4, process system：The cooling procedure of the present invention be water cooling-it is air-cooled-the three-stage refrigerating mode of water cooling.Japan Patent
JP2010063547 is then that the two-period form of air-cooled-water cooling cools down.Canadian Patent CA2775031 is using two different cooling speed
Degree.
Beneficial effects of the present invention：
Hot-rolled high-strength high-strength steel sheet of the present invention, uses fairly simple composition design, basic intensified element be C,
Mn adds Nb, Ti on a small quantity；In process of production, relatively simple production technology is used, in conventional laminar flow cooling after hot rolling
A sub-sectional cooling pattern is increased in sequence, is readily produced.
The steel plate of the present invention produced is designed according to mentioned component design and processes, and there is high uniform elongation so that
The excellent cold-workability exhibiting of steel plate of the present invention has original in manufacture shape more complex automobile chassis and automobile structure
Advantage.
Description of the drawings
Fig. 1 is the microstructure picture of C steel of the embodiment of the present invention.
Specific implementation mode
With reference to embodiment and attached drawing, the present invention will be further described.
Table 1 is the chemical composition of steel of the embodiment of the present invention, and the ingredient of A~E steel steel embodiment of the present invention, H, G steel are with normal
The steel of rule, which is used as, compares steel.Table 2 is the manufacturing process of steel of the embodiment of the present invention, and table 3 is the performance of steel of the embodiment of the present invention.Thickness
Test for the mechanical property of the steel plate of 3mm, mechanical property is carried out by GB6397-86 standards, and comparative example is the normal of close intensity
Advise steel plate.
Table 1
As shown in Figure 1, the microstructure of C steel plates of the embodiment of the present invention is the bainite of ferrite+a small amount of.
Table 2
* embodiment and comparative example tensile test specimen scale distance are 50mm.
The mechanical property of 3 embodiment steel steel compared with of table
Claims (8)
1.400-500MPa grades high uniform elongation hot continuous-milling steel plate, composition by weight percent are：
C 0.04~0.08%,
Si 0~1.6%,
Mn 0.8~1.5%,
P≤0.035%,
S≤0.001%,
Al 0.025~0.060%,
N≤0.0060%,
And more than one element in Ti≤0.03%, Nb≤0.05% and Ca≤0.0050%,
Remaining is Fe and inevitable impurity.
2. 400-500MPa grades high uniform elongation hot continuous-milling steel plate as described in claim 1, characterized in that steel plate it is microcosmic
It is organized as the bainite of 10-30% and the ferrite of 70-90%, wherein ferritic ratio of the length-width ratio 1.0~1.2
Not less than 80%.
3. 400-500MPa grades high uniform elongation hot continuous-milling steel plate as claimed in claim 1 or 2, characterized in that steel plate is bent
It is 20% or more to take intensity >=460MPa, tensile strength >=550MPa, uniform elongation, and -40 DEG C of Charpy-V impact power is (single
Value) >=100J, Kca (- 10 ° DEG C) >=6500N/mm1.5。
4. the high uniform elongation hot continuous-milling steel plate of 400-500MPa grades as described in claims 1 or 2 or 3, characterized in that steel plate
Thickness≤12mm.
5. the manufacturing method of 400-500MPa grades high uniform elongation hot continuous-milling steel plate as described in claim 1, characterized in that
Include the following steps：
1) it smelts, cast
It smelted by ingredient described in claim 1, be cast as base；
2) heating of plate blank, heating and temperature control is at 1150~1250 DEG C；
3) it rolls, is rolled at a temperature of not less than Ar3, rolling reduction 80-95%, 800~900 DEG C of finishing temperature；
4) steel plate after finish to gauge is as cold as 600~750 DEG C with the cooling velocity of 50~150 DEG C/s, then with the cooling of 3~10 DEG C/s
Speed cools down 2~10 seconds in air, is then cooled to 350~500 DEG C with the cooling velocity of 100 DEG C/s or more again and rolls up
It takes, is then air-cooled to room temperature.
6. the manufacturing method of 400-500MPa grades high uniform elongation hot continuous-milling steel plate as claimed in claim 5, characterized in that
The microstructure of steel plate is the bainite of 10-30% and the ferrite of 70-90%, wherein iron of the length-width ratio 1.0~1.2
The ratio of ferritic is not less than 80%.
7. such as the manufacturing method of 400-500MPa grades high uniform elongation hot continuous-milling steel plate described in claim 5 or 6, feature
It is that steel plate yield strength >=460MPa, tensile strength >=550MPa, uniform elongation are 20% or more.
8. the manufacturing method of the high uniform elongation hot continuous-milling steel plate of 400-500MPa grades as described in claim 5 or 6 or 7,
It is characterized in, steel plate thickness≤12mm.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109576581A (en) * | 2018-11-30 | 2019-04-05 | 宝山钢铁股份有限公司 | A kind of great surface quality, low yield strength ratio hot-rolled high-strength steel plate and manufacturing method |
| CN112522597A (en) * | 2019-09-19 | 2021-03-19 | 宝山钢铁股份有限公司 | Boron-containing high-reaming-hole steel and production method thereof |
| CN115572902A (en) * | 2022-09-30 | 2023-01-06 | 吉林建龙钢铁有限责任公司 | Steel for integrated wheel hub and preparation method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101565794A (en) * | 2008-04-22 | 2009-10-28 | 宝山钢铁股份有限公司 | High-strength hot rolling automotive frame steel plate and manufacturing method thereof |
| JP2010063547A (en) * | 2008-09-09 | 2010-03-25 | Three M Innovative Properties Co | Fingertip infection prevention sheet for acupuncture |
| CN101928881A (en) * | 2009-06-26 | 2010-12-29 | 宝山钢铁股份有限公司 | Hot rolling high-chambering steel plate with tensile strength of 590 MPa and manufacturing process thereof |
| CN102549188A (en) * | 2009-09-30 | 2012-07-04 | 杰富意钢铁株式会社 | Steel plate having low yield ratio, high strength and high uniform elongation and method for producing same |
| CN102650017A (en) * | 2012-05-25 | 2012-08-29 | 宝山钢铁股份有限公司 | Hot-rolled steel plate and manufacturing method thereof |
| KR20130036075A (en) * | 2009-11-20 | 2013-04-09 | 신닛테츠스미킨 카부시키카이샤 | Thick steel plate for ship hull and process for production thereof |
| CN103667880A (en) * | 2013-11-29 | 2014-03-26 | 宝山钢铁股份有限公司 | High hole expansion steel plate with tensile strength of 440MPa and manufacturing method thereof |
-
2017
- 2017-03-24 CN CN201710183338.9A patent/CN108624818A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101565794A (en) * | 2008-04-22 | 2009-10-28 | 宝山钢铁股份有限公司 | High-strength hot rolling automotive frame steel plate and manufacturing method thereof |
| JP2010063547A (en) * | 2008-09-09 | 2010-03-25 | Three M Innovative Properties Co | Fingertip infection prevention sheet for acupuncture |
| CN101928881A (en) * | 2009-06-26 | 2010-12-29 | 宝山钢铁股份有限公司 | Hot rolling high-chambering steel plate with tensile strength of 590 MPa and manufacturing process thereof |
| CN102549188A (en) * | 2009-09-30 | 2012-07-04 | 杰富意钢铁株式会社 | Steel plate having low yield ratio, high strength and high uniform elongation and method for producing same |
| KR20130036075A (en) * | 2009-11-20 | 2013-04-09 | 신닛테츠스미킨 카부시키카이샤 | Thick steel plate for ship hull and process for production thereof |
| CN102650017A (en) * | 2012-05-25 | 2012-08-29 | 宝山钢铁股份有限公司 | Hot-rolled steel plate and manufacturing method thereof |
| CN103667880A (en) * | 2013-11-29 | 2014-03-26 | 宝山钢铁股份有限公司 | High hole expansion steel plate with tensile strength of 440MPa and manufacturing method thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109576581A (en) * | 2018-11-30 | 2019-04-05 | 宝山钢铁股份有限公司 | A kind of great surface quality, low yield strength ratio hot-rolled high-strength steel plate and manufacturing method |
| CN112522597A (en) * | 2019-09-19 | 2021-03-19 | 宝山钢铁股份有限公司 | Boron-containing high-reaming-hole steel and production method thereof |
| CN115572902A (en) * | 2022-09-30 | 2023-01-06 | 吉林建龙钢铁有限责任公司 | Steel for integrated wheel hub and preparation method thereof |
| CN115572902B (en) * | 2022-09-30 | 2023-08-22 | 吉林建龙钢铁有限责任公司 | Integrated steel for wheel hub and preparation method thereof |
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Application publication date: 20181009 |