CN101812640A - In-situ composite high-strength thick steel plate and manufacturing method thereof - Google Patents
In-situ composite high-strength thick steel plate and manufacturing method thereof Download PDFInfo
- Publication number
- CN101812640A CN101812640A CN200910046473A CN200910046473A CN101812640A CN 101812640 A CN101812640 A CN 101812640A CN 200910046473 A CN200910046473 A CN 200910046473A CN 200910046473 A CN200910046473 A CN 200910046473A CN 101812640 A CN101812640 A CN 101812640A
- Authority
- CN
- China
- Prior art keywords
- steel
- percent
- steel plate
- casting
- composite high
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses an in-situ composite high-strength thick steel plate and a manufacturing method thereof. The in-site composite high-strength thick steel plate comprises the following components in mass percentage: 0.1 to 0.2 percent of C, 1.2 to 1.8 percent of Mn, 0.2 to 0.3 percent of Si, less than or equal to 0.015 percent of P, less than or equal to 0.002 percent of S, 0.15 to 0.2 percent of Cu, 0.2 to 0.25 percent of Ni, 0.02 to 0.03 percent of Nb, 0.01 to 0.015 percent of Ti, less than or equal to 0.04 percent of Al, less than or equal to ppm of N, less than or equal to 20 ppm of O and the balance of Fe and inevitable impurities, wherein the carbon equivalent Ceq which is the ratio of C+(Mn+Si) to 6+(Ni+Cu) to 15+(Cr+Mo+V) is 0.36 to 0.58; and the steel plate thickness is 50 to 400 millimeters. In the invention, the bottom of the produced steel ingot has no negative segregation, the section concentration is almost equal to the molten steel concentration, and the positive segregation is formed on the upper part of the steel ingot; and the tensile strength and the yield strength of the steel can be greatly improved by solute elements such as C and Mn in the steel and by solution strengthening. The upper strength of billets is improved by one-way solidification manufacturing technology starting from the bottom by the segregations of the elements such as C and Mn at the end of the solidification.
Description
Technical field
The present invention relates to clad steel plate and manufacture method thereof, particularly a kind of situ composite high-strength thick steel plate and manufacture method thereof.
Background technology
Along with development of modern industry, the demand of matrix material is increased day by day, composite study, use and also obtained development fast.Composite steel sheet billet production commonly used is that this method can be made the clad steel plate of unlike material by alternately closely stack and making of one deck basic steel and other steel more than one deck at least, but its rolling difficulty is big, complex manufacturing.
Chinese patent application numbers 200410018300.9 disclose by ultra high temp gradient high speed directional freeze prepare the fibrous directed γ of rule-(Fe, Mn)
3The C eutectic autogenous composite material, its research method provides new thinking for the preparation of eutectic composites, and still, this method needs ultra high temp gradient high speed directional freeze condition, realizes difficulty in being applied to the large size product.
Metal can only be worked as in liquid phase and the solid phase solute and spread fully and just can reach absolute equilibrium when even and solidify in process of setting.But absolute curing condition can not run into aborning, because the spread coefficient of solute has only 10 of temperature diffusion
-3～10
-5Doubly, particularly the spread coefficient of solute in solid phase is littler, and therefore, when solute did not also have enough time to spread, temperature reduced a lot already, and solid-liquid interface is pushed ahead greatly, and the solid phase of new constituent crystallizes out again.In the actual production process of setting, produce solute and distribute again, certainly lead to macrosegregation and microsegregation.Common steel ingot inevitably exists V-type segregation, reverse V-shaped segregation, defective such as loose, and these tend to make plate quality to go wrong, and usually will stop or reduce the formation of this macrosegregation in therefore producing, to improve the quality of products.
But by the unidirectional solidification manufacturing technology that begins from the bottom, the segregation behavior of steel ingot and former steel ingot difference are very big, the steel ingot bottom does not almost have negative segregation, section concentration almost equates with molten steel concentration, and there is positive segregation in the top of steel ingot, and this is just meeting and begins to solidify the positive segregation that part concentration is low, final section concentration is high and form feature.On the other hand, the strengthening mechanism theory of steel has illustrated that solute element C, the N in the steel, Mn etc. can make the tensile strength of steel, yield strength improve greatly by solution strengthening.Show that according to test-results every increase 0.1%C can make tensile strength on average improve 70MPa, yield strength on average improves 28MPa.Therefore can utilize the increase of positive segregation district solute concentration to improve the intensity of steel, thereby produce the situ composite high-strength steel plate.
Summary of the invention
The purpose of this invention is to provide a kind of situ composite high-strength thick steel plate and manufacture method thereof, on the unidirectional solidification manufacturing technology basis that begins with the bottom, the segregation of elements such as end of a period C, Mn on steel ingot top solidified in utilization, to form a large amount of carbide, thereby obtain enough hardness, and guarantee enough welding adaptability, final steel plate upper strength and the wear resisting property of improving, and the bottom steel plate satisfies requirement of strength as the matrix steel plate, have good toughness again, thereby produce situ composite high-strength thick steel plate.
For achieving the above object, technical scheme of the present invention is,
Chemical ingredients satisfies: C:0.1-0.2%, Mn:1.2-1.8%, Si:0.2-0.3%, P :≤0.015%, S :≤0.002%, Cu:0.15-0.2%, Ni:0.2-0.25%, Nb:0.02-0.03%, Ti:0.01-0.015%, Al :≤0.04%, N≤50ppm, O≤20ppm, all the other are Fe and unavoidable impurities, carbon equivalent 0.36～0.58.Be suitable for producing the steel plate of thickness specification 50～400mm.Wherein, carbon equivalent Ceq=C+ (Mn+Si)/6+ (Ni+Cu)/15+ (Cr+Mo+V)/5.
The casting of steel ingot is made the thickness specification from 300～800mm by extra-thick plate blank unidirectional solidification device, and the heavy maximum of ingot can reach 80 tons unidirectional solidification steel ingot.
Technology controlling and process requires as follows in the casting cycle:
When beginning casting bottom cooling chassis water flowing is cooled off, and the heat that guarantees to take out of from the bottom cooling is greater than 90%;
Keep during the casting beginning progressively adding near 2～5 tons/minute less than 2 tons of/minute slower casting rates, the control of casting rate helps controlling the liquid fluctuating of molten steel;
The casting molten steel reaches 1/2～2/3 o'clock adding die casting granular protecting cinder of casting total amount, does not thoroughly form inclusion to prevent the covering slag come-up, reduces the quality of steel;
Heating board is placed on the ingot mold top in advance, and cast ends and manually pushes, and installs additional and finishes the bonnet top cover, guarantees molten steel top heat.
Secondly, the rolling technology flow process of steel ingot is: process furnace → de-scaling → low speed is depressed rolling → cooling greatly.
Hot rolling technology is: steel ingot is heated to 1120～1200 ℃, is incubated 12～15 hours; Be to guarantee gripping angle and distortion perviousness, begin to adopt when rolling the roll speed of about 1～3m/s carry out low speed depress greatly rolling, recrystallize stage rolling pass deformation 15～35%, non-recrystallization stage cumulative deformation 〉=45%; Roll the back be chilled to 500 ℃ with 5～10 ℃/second after slow cooling.
The invention has the beneficial effects as follows,
1. chemical ingredients is a target with the control carbon equivalent, and the design mix carbon equivalent is 0.36～0.58, can satisfy the requirement of welding property.
2. the bottom water flowing is cold by force when casting, adiabatic, top adds heating board all around, effectively guarantees molten steel unidirectional solidification condition, makes component segregation in the steel ingot top, forms the composite bed that improves intensity.Compare with traditional steel ingot, the position of segregation layer changes, and effectively guarantees to roll back steel plate Z to performance.
3. by the clad steel plate of unidirectional solidification casting production, matrix and high strength composition of layer effectively guarantee the binding ability of composite bed and matrix along the thickness direction graded.
4. control casting rate and covering slag joining day, effectively control strong convection current of molten steel and liquid fluctuating, prevent to roll up slag, help Control and Inclusion Removal, improve steel.
5. to adopt low speed to depress greatly rolling for the operation of rolling, helps rolling deformation and go deep into the thickness of slab middle part, improves thickness of slab direction homogeneity of structure, guarantees that effectively steel plate Z is to performance.
Description of drawings
Fig. 1 is the embodiment of the invention 2 steel ingot thickness direction Hardness Distribution;
The composite bed tensile strength that Fig. 2 provides for the present invention and the comparison of matrix.
Embodiment
Below in conjunction with specific examples the present invention is further described.
Situ composite high-strength thick steel plate embodiment chemical ingredients of the present invention is referring to table 1,
Table 1 unit: wt%
| Embodiment | ??C | ??Si | ??Mn | ??P | ??S | ??Cu | ??Ni | ??Nb | ??Al | ??Ti | ??O??ppm | ??N??ppm |
| ??1 | ??0.10 | ??0.220 | ??1.20 | ??0.015 | ??0.0018 | ??0.15 | ??0.25 | ??0.024 | ??0.036 | ??0.013 | ??16 | ??40 |
| ??2 | ??0.15 | ??0.265 | ??1.43 | ??0.015 | ??0.0018 | ??0.16 | ??0.24 | ??0.024 | ??0.037 | ??0.013 | ??16 | ??40 |
| ??3 | ??0.20 | ??0.270 | ??1.76 | ??0.015 | ??0.0018 | ??0.18 | ??0.24 | ??0.024 | ??0.036 | ??0.012 | ??16 | ??40 |
| ??4 | ??0.13 | ??0.210 | ??1.22 | ??0.014 | ??0.0017 | ??0.15 | ??0.20 | ??0.021 | ??0.038 | ??0.010 | ??18 | ??42 |
| ??5 | ??0.18 | ??0.295 | ??1.80 | ??0.012 | ??0.0020 | ??0.20 | ??0.25 | ??0.029 | ??0.035 | ??0.015 | ??19 | ??45 |
| ??6 | ??0.16 | ??0.24 | ??1.52 | ??0.015 | ??0.0019 | ??0.17 | ??0.21 | ??0.026 | ??0.037 | ??0.014 | ??16 | ??40 |
By the unidirectional solidification device thickness of having cast is the thick steel ingot of 500mm, is rolled into the steel plate that thickness is 100mm, and rolling technological parameter is referring to table 2:
Table 2
| Embodiment | Heating temperature ℃ | Roughing finishing temperature ℃ | Finish rolling finishing temperature ℃ | Finish rolling accumulative total deflection % | Roll speed m/s | Speed of cooling ℃/s |
| ??1 | ??1150 | ??950 | ??850 | ??45 | ??1.5 | ??5 |
| ??2 | ??1150 | ??950 | ??850 | ??50 | ??1.5 | ??7 |
| ??3 | ??1150 | ??950 | ??850 | ??50 | ??1 | ??10 |
| ??4 | ??1120 | ??900 | ??800 | ??55 | ??3 | ??8 |
| ??5 | ??1200 | ??980 | ??880 | ??55 | ??2 | ??10 |
| ??6 | ??1160 | ??960 | ??860 | ??50 | ??2.5 | ??8 |
Spectrochemistry composition test has been carried out at the steel ingot top, analyzed the segregation situation of C, steel ingot thickness direction C concentration distribution is referring to table 3:
Table 3 unit: wt%
| The position | Example 1 | Example 2 | Example 3 |
| Apart from top 10mm | ??0.28 | ??0.35 | ??0.45 |
| Apart from top 20mm | ??0.25 | ??0.30 | ??0.41 |
| Apart from top 50mm | ??0.24 | ??0.28 | ??0.37 |
| Apart from top 100mm | ??0.20 | ??0.25 | ??0.31 |
| Matrix | ??0.12 | ??0.15 | ??0.21 |
Referring to Fig. 1, it has shown embodiment 2 steel ingot thickness direction Hardness Distribution, therefrom finds out, hardness value has two zones from steel ingot top to bottom, and one is that another is the hardness value stabilized zone apart from the high zone of the above hardness of steel ingot top 100mm.Therefore not being both owing to the isocyatic difference of different positions carbon causes of steel ingot hardness illustrated also that the segregation layer is positioned at the steel ingot top, consistent with the composition analysis in the table 3 by the steel ingot of unidirectional solidification casting.
Rolling from Ingot is made the steel plate that thickness is 100mm, and the mechanical property of rolling back steel matrix (embodiment 2) is referring to table 4:
Table 4
Referring to Fig. 2, it has provided the comparison of composite bed tensile strength and matrix, therefrom finds out, suitably adjusts the speed of cooling that the back steel plate is rolled in solution strengthening amount of element such as carbon, manganese and raising, when can improve matrix strength, further improves the intensity of composite bed.
Claims (3)
1. situ composite high-strength thick steel plate, its composition quality per-cent is: C:0.1-0.2%, Mn:1.2-1.8%, Si:0.2-0.3%, P≤0.015%, S≤0.002%, Cu:0.15-0.2%, Ni:0.2-0.25%, Nb:0.02-0.03%, Ti:0.01-0.015%, Al≤0.04%, N≤50ppm, O≤20ppm, all the other are Fe and unavoidable impurities; Wherein, carbon equivalent Ceq=C+ (Mn+Si)/6+ (Ni+Cu)/15+ (Cr+Mo+V)/5, carbon equivalent 0.36～0.58; Steel plate thickness 50～400mm.
2. the manufacture method of situ composite high-strength thick steel plate as claimed in claim 1, it comprises the steps:
1) smelts, is cast into steel ingot by mentioned component;
Keep casting rate during the casting beginning, progressively add near 2～5 tons/minute less than 2 tons/minute;
The casting molten steel reaches 1/2～2/3 o'clock adding die casting granular protecting cinder of casting total amount, does not thoroughly form inclusion to prevent the covering slag come-up, reduces the quality of steel;
2) hot rolling,
Steel ingot is heated to 1120～1200 ℃, is incubated 12～15 hours, de-scaling then; Be to guarantee gripping angle and distortion perviousness, begin to adopt when rolling the roll speed of 1～3m/s carry out low speed depress greatly rolling, recrystallize stage rolling pass deformation 15～35%, non-recrystallization stage cumulative deformation 〉=45%; Roll the back be chilled to 500 ℃ with 5～10 ℃/second after slow cooling.
3. the manufacture method of situ composite high-strength thick steel plate as claimed in claim 2 is characterized in that, extra-thick plate blank unidirectional solidification device is adopted in casting, makes the thickness specification from 300～800mm, and the heavy maximum of ingot can reach 80 tons unidirectional solidification steel ingot.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2009100464734A CN101812640B (en) | 2009-02-23 | 2009-02-23 | In-situ composite high-strength thick steel plate and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2009100464734A CN101812640B (en) | 2009-02-23 | 2009-02-23 | In-situ composite high-strength thick steel plate and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101812640A true CN101812640A (en) | 2010-08-25 |
| CN101812640B CN101812640B (en) | 2011-11-23 |
Family
ID=42620007
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2009100464734A Expired - Fee Related CN101812640B (en) | 2009-02-23 | 2009-02-23 | In-situ composite high-strength thick steel plate and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101812640B (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105088095A (en) * | 2015-08-27 | 2015-11-25 | 舞阳钢铁有限责任公司 | High-plasticity and high-tenacity thick steel plate and production method thereof |
| CN105107842A (en) * | 2015-09-15 | 2015-12-02 | 辽宁科技大学 | Method and device for producing thick plate and super-thick plate by reducing and roll cladding |
| CN105274433A (en) * | 2014-07-16 | 2016-01-27 | 鞍钢股份有限公司 | Super-thick steel plate and composite production method thereof |
| CN106216947A (en) * | 2016-07-26 | 2016-12-14 | 舞阳钢铁有限责任公司 | A kind of production method of big thickness flaw detection steel plate |
| CN107557690A (en) * | 2016-06-30 | 2018-01-09 | 鞍钢股份有限公司 | The super-thick steel plate and its manufacture method of a kind of low temperature resistant and anti-lamellar tearing |
| CN113198993A (en) * | 2021-04-19 | 2021-08-03 | 鞍钢集团北京研究院有限公司 | Method for reducing center segregation of low alloy steel continuous casting billet |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1116433C (en) * | 2001-02-20 | 2003-07-30 | 上海交通大学 | Nodular eutectic pearlite steel base authigenic composite material |
| CN100588734C (en) * | 2007-11-27 | 2010-02-10 | 湖南华菱湘潭钢铁有限公司 | High-strength shipbuilding section and production method thereof |
-
2009
- 2009-02-23 CN CN2009100464734A patent/CN101812640B/en not_active Expired - Fee Related
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105274433A (en) * | 2014-07-16 | 2016-01-27 | 鞍钢股份有限公司 | Super-thick steel plate and composite production method thereof |
| CN105088095A (en) * | 2015-08-27 | 2015-11-25 | 舞阳钢铁有限责任公司 | High-plasticity and high-tenacity thick steel plate and production method thereof |
| CN105107842A (en) * | 2015-09-15 | 2015-12-02 | 辽宁科技大学 | Method and device for producing thick plate and super-thick plate by reducing and roll cladding |
| CN107557690A (en) * | 2016-06-30 | 2018-01-09 | 鞍钢股份有限公司 | The super-thick steel plate and its manufacture method of a kind of low temperature resistant and anti-lamellar tearing |
| CN107557690B (en) * | 2016-06-30 | 2019-03-26 | 鞍钢股份有限公司 | The super-thick steel plate and its manufacturing method of a kind of low temperature resistant and anti-lamellar tearing |
| CN106216947A (en) * | 2016-07-26 | 2016-12-14 | 舞阳钢铁有限责任公司 | A kind of production method of big thickness flaw detection steel plate |
| CN113198993A (en) * | 2021-04-19 | 2021-08-03 | 鞍钢集团北京研究院有限公司 | Method for reducing center segregation of low alloy steel continuous casting billet |
| CN113198993B (en) * | 2021-04-19 | 2022-04-26 | 鞍钢集团北京研究院有限公司 | Method for reducing center segregation of low alloy steel continuous casting billet |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101812640B (en) | 2011-11-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN113278896B (en) | Fe-Mn-Al-C series high-strength low-density steel and preparation method thereof | |
| JP6584961B2 (en) | Copper-rich nanocluster reinforced ultra high strength ferritic steel and method for producing the same | |
| CN101812640B (en) | In-situ composite high-strength thick steel plate and manufacturing method thereof | |
| CN110760757B (en) | Low-cost strengthening process of hot-rolled steel bar | |
| CN110172641B (en) | Fine-grain high-toughness hot-work die steel and preparation method thereof | |
| KR101623290B1 (en) | High strength austenitic stainless steel, and preparation method thereof | |
| CN102226250B (en) | Hot rolled steel plate with yield strength being 700MPa and preparation method thereof | |
| CN103397275A (en) | Martensite series wear-resistant steel and preparation method thereof | |
| WO2017173950A1 (en) | Lightweight steel and steel sheet with enhanced elastic modulus, and manufacturing method thereof | |
| DE112013000841T5 (en) | A method of producing a weather-resistant continuous strip steel having a high strength of 700 MPa | |
| CN105441790A (en) | Steel plate with low welding crack sensitivity and manufacturing method thereof | |
| CN107779746B (en) | Ultra-fine grain alloy steel with ultrahigh strength, high toughness, corrosion resistance, oxidation resistance and preparation method thereof | |
| CN106868399B (en) | A kind of two-phase TRIP steel strips and preparation method thereof | |
| CN102605252A (en) | Steel plate with yield strength grade of 1030MPa and manufacturing method thereof | |
| CN107043890B (en) | A kind of 1.5~3.0mm of thickness yield strength is greater than the Hot Rolling Automobile steel and its manufacturing method of 700MPa | |
| CN104947000A (en) | High-strength steel with yield strength of 700MPa and TMCP manufacturing method | |
| CN102899589A (en) | High-strength non-tempered bainite steel and preparation method thereof | |
| CN104831167A (en) | Q550E high-strength steel hot rolled coil and production method thereof | |
| CN103981463A (en) | X70 bend hot-rolled flat plate having excellent toughness and production method thereof | |
| CN104342598A (en) | Production method of hot rolled steel strip for 600 MPa-level automotive frame | |
| CN110616361A (en) | Production method of steel for annealing-free nitriding | |
| CN114959420A (en) | Preparation method of non-quenched and tempered steel for cylinder of plastic molding machine for producing round billet | |
| CN104060170A (en) | Hot-rolled steel sheet and production method thereof | |
| CN101429627A (en) | Austenite valve steel and technique for producing the same | |
| CN104593665A (en) | Method for manufacturing thick hot-rolled dual-phase steel based on CSP (Compact Strip Production) process |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20111123 Termination date: 20140223 |