CN101255534B - Blast furnace hood steel - Google Patents
Blast furnace hood steel Download PDFInfo
- Publication number
- CN101255534B CN101255534B CN2008100470092A CN200810047009A CN101255534B CN 101255534 B CN101255534 B CN 101255534B CN 2008100470092 A CN2008100470092 A CN 2008100470092A CN 200810047009 A CN200810047009 A CN 200810047009A CN 101255534 B CN101255534 B CN 101255534B
- Authority
- CN
- China
- Prior art keywords
- steel
- weight
- blast furnace
- rel
- strength
- 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.)
- Expired - Fee Related
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to the field of low alloyed steel, which solves the problem that blast furnace can not be used for 15 years and more and used under 500 to 700 DEG C high temperature in current technology, which is caused by its low mechanical strength. The technical measure is as follows: the steel is composed of 0.05% to 0.12% by weight of C, 0.25% to 0.40% by weight of Si, 1.20% to 1.70% by weight of Mn, no more than 0.018% by weight of P, no more than 0.008% by weight of S, 0.008% to 0.03% by weight of Ti, 0.02% to 0.05% by weight of Nb, 0.236% to 0.40% by weight of W, no more than 0.3% by weight of Cr, no more than 0.03% by weight of Als, and the balance Fe and unavoidable impurity. The steel has extremely high strength and impact toughness, the room temperature mechanical properties measured are as follows: ReL >=430MPa, Rm>=575MPa, A5>=23% and 0 DEG C Akv>=175J; the high temperature mechanical properties are as follows: under 500 DEG C, ReL>=335MPa, Rm>=378MPa; under 700 DEG C, ReL reaches 150 to 215MPa, and is capable of resisting strength loss caused by local heat shock.
Description
Technical field
The present invention relates to low alloying rings territory, refer to be suitable for R under 500～700 ℃ of high temperature particularly
m〉=378MPa has excellent impelling strength simultaneously, 0 ℃ of A
KvThe high intensity blast furnace shell steel of 〉=175J.
Background technology
Blast furnace ironmaking is the important step of Iron and Steel Production, build big blast furnace one-time investment more than hundred million yuan, and in the expense of repairing at every turn need be with 1000～2,000 ten thousand yuan, in repair the stopping production that also will cause 50～60 days, can bring huge economic benefit the work-ing life that therefore prolongs blast furnace.Last furnace shell as blast-furnace equipment chief component, one of the three big key elements that blast furnace overhaul must be changed (furnace shell, bricking, cooling apparatus), the importance of its status is self-evident, rationally selects shell steel for use, can improve the furnace shell life-span, for the production of blast furnace longevityization provides strong assurance.
In the later stage eighties, because the raising of blast-furnace technique integral level, proposed to prolong the imagination in furnace life, strive reaching work-ing life the target of 8-10, traditional carbon steel can not satisfy the requirement of maximization and modernized blast furnace new process of production far away, so the numerous and confused exploitation of each iron and steel producer and other 490MPa level low alloy steel series of use higher intensity level.External comparatively typical steel grade has SM50B, the SM50C steel of Japan, domestic 490MPa level furnace shell steel, the WSM50C steel of use Wuhan Iron and Steel Plant development comparatively generally, the BB502 steel and the BB503 steel of Baosteel development.The Chemical Composition of its steel grade and mechanical property see Table 1, shown in the table 2:
The Chemical Composition (Wt%) of the present commercial furnace shell steel of table 1
The mechanical property of the present commercial furnace shell steel of table 2
| The trade mark | Rel(MPa) | Rm(MPa) | A(％) | Clod wash (180 °) | A kv(J) |
| WSM50C | ≥295 | 490～610 | ≥17 | D＝3a | 0℃，≥47 |
| SM50B | ≥295 | 490～610 | ≥17 | D＝3a | 0℃，≥27 |
| SM50C | ≥295 | 490～610 | ≥17 | D＝3a | 0℃，≥47 |
These steel grades have all been realized above-mentioned requirements, and blast furnace reaches 8～10 years work-ing life, and furnace life repaiies in not.Because the development and the social requirement of situation, it has interim advance, maximum is brought into play throughput, reducing production costs then has its inadaptability for answering at present, promptly can not satisfy and to prolong blast furnace more and reach 15 years and above requirement work-ing life, because of its physical strength is lower, incompatibility working conditions under 500～700 ℃ of high temperature.
Summary of the invention
The objective of the invention is to overcome above-mentioned deficiency, provide a kind of and can prolong that blast furnace reached 15 years work-ing life and above have a R under extremely excellent normal temperature and 500～700 ℃ of high temperature
m〉=378Mpa has the i.e. 0 ℃ of A of excellent impelling strength simultaneously
KvThe high-strength mechanical properties of 〉=175J, the blast furnace hood steel of high-strong toughness coupling.
Realize the technical scheme of above-mentioned purpose:
Technical scheme one:
Blast furnace hood steel, by the following chemical ingredients of forming by weight percentage ratio (%) be: C:0.05～0.12, Si:0.25～0.40, Mn:1.20～1.70, P :≤0.018, S :≤0.008, Ti:0.008～0.03, Nb:0.02～0.05,
W:0.236～0.40, Cr :≤0.3, Als≤0.03, all the other are Fe and unavoidable impurities.
It is: the weight percentage of W is 0.236～0.30.
Technical scheme two:
Blast furnace hood steel, by the following chemical ingredients of forming by weight percentage ratio (%) be: C:0.05～0.12, Si:0.25～0.40, Mn:1.20～1.70, P :≤0.018, S :≤0.008, Ti:0.008～0.03, Nb:0.02～0.05, Mo:0.2476～0.25, Cr :≤0.3, Als≤0.03, all the other are Fe and unavoidable impurities.
Technical scheme three:
Blast furnace hood steel, by the following chemical ingredients of forming by weight percentage ratio (%) be: C:0.05～0.12, Si:0.25～0.40, Mn:1.20～1.70, P :≤0.018, S :≤0.008, Ti:0.008～0.03, Nb:0.02～0.05, W:0.245～0.30, Mo:0.13～0.20, Cr :≤0.3, Als≤0.03, all the other are Fe and unavoidable impurities.
The reasons are as follows of the effect of C, Si, Mn, P, S, Ti, Nb, W, Mo and limited amount among the present invention:
Carbon (C): carbon is one of most important solution strengthening element in the steel, and elements such as W, Mo can form carbide in carbon and the steel, help improving the intensity of steel, especially the hot strength of steel.Therefore the too high rapid decline that then causes toughness and weldability of carbon content on the basis of proof strength, be limited to 0.05～0.12 with carbon.
Silicon (Si): silicon mainly is the intensity that improves steel with the solution strengthening form, also be simultaneously the deoxidant element in the steel, but content then can reduce the toughness and the welding property of steel as being higher than 0.40.
Manganese (Mn): manganese is solution strengthening element important in the steel, can improve hardening capacity, can reduce austenitic transformation and become ferritic transformation temperature, enlarge the austenite region in the iron-carbon diagram, promote the middle temperature structural transformation of steel, help refining grain size, improve the yield strength and the impelling strength of steel.
Phosphorus (P), sulphur (S): higher phosphorus content can increase substantially the weathering resistance of steel, but phosphorus in steel, have cause segregation easily, worsen welding property, significantly reduce steel low-temperature impact toughness, improve brittle transition temperature, so, consider that hardness of steel of the present invention is higher, control P≤0.018; Sulphur easily combines generation MnS and is mingled with manganese, sulphur also influences the low-temperature impact toughness of steel.Therefore, the present invention should reduce as far as possible phosphorus, element sulphur to rigidity can disadvantageous effect, by molten iron being carried out means such as dark desulfurization pre-treatment, vacuum-treat, control phosphorus, sulphur content, thereby alleviate its disadvantageous effect.
Tungsten (W): tungsten can promote the middle temperature structural transformation of steel, can form carbide when tempering separates out, thereby increase the high tempering drag of steel, molybdenum can also be avoided the embrittlement phenomenon (temper brittleness) that steel occurs when 400 ℃～500 ℃ left and right sides tempering in addition, but molybdenum content is low excessively, do not have effect, therefore the high embrittlement that can cause steel on the contrary controls W in 0.10～0.40 scope.
Molybdenum (Mo): the effect and the tungsten of molybdenum are similar, and its effect roughly is equivalent to molybdenum, both add simultaneously its effect add more separately a kind of good.
The present invention has following advantage:
1. steel of the present invention has high intensity and impelling strength, and room temperature actual measurement mechanical property is: ReL 〉=430MPa, Rm 〉=575MPa, A
5〉=23%, 0 ℃ of A
Kv〉=175J, obdurability coupling is very excellent, is greatly improved than the mechanical property of present commercial furnace shell steel,
2. steel mechanical behavior under high temperature excellence of the present invention, ReL 〉=335MPa in the time of 500 ℃, Rm 〉=378MPa, ReL still can reach 150～215MPa in the time of 700 ℃, when being applied to last furnace shell, can resisting localized heat and impact the loss of strength that causes.
Embodiment
The present invention adopts 50 kilograms of vacuum induction furnace smelting steel ingots, or adopts the technology of converter smelting Clean Steel, that is: pre-desulphurised hot metal, converter top bottom blowing, through vacuum-treat, pour into slab, adopt the hot rolling production technique again, roll the backlash water cooling, the concrete operation of rolling comprises:
Slab is heated to 1200～1250 ℃, heat-up time 〉=150min; Elder generation's roughing, every time draft 〉=10%, roughing end temp are 〉=1000 ℃; Finish rolling again is being lower than in 950 ℃, accumulation draft ∑ ε i 〉=60%, finishing temperature: 790 ℃～840 ℃; Steel plate rolls the backlash water cooling, and 700 ± 20 ℃ of red temperature are returned in control.
As in order further to improve impelling strength, can carry out temper to this hot rolling attitude steel plate.When the tempering system that adopts is: during 640 ℃+3min/mm, 0 ℃ of impact toughness value of steel plate can further improve to 250J, and obvious variation takes place the intensity of steel plate hardly after the tempering simultaneously.
Table 3 embodiment steel plate Chemical Composition (wt%)
Table 4 steel plate mechanical property (not carrying out temper)
Pass through the mechanical property after the temper behind table 5 steel plate rolling again
Claims (4)
1. blast furnace hood steel, by the following chemical ingredients of forming by weight percentage ratio (%) be: C:0.05～0.12, Si:0.25～0.40, Mn:1.20～1.70, P :≤0.018, S :≤0.008, Ti:0.008～0.03, Nb:0.02～0.05, W:0.236～0.40, Cr :≤0.3, Als≤0.03, all the other are Fe and unavoidable impurities.
2. blast furnace hood steel as claimed in claim 1 is characterized in that: the weight percentage of W is 0.236～0.30.
3. blast furnace hood steel, by the following chemical ingredients of forming by weight percentage ratio (%) be: C:0.05～0.12, Si:0.25～0.40, Mn:1.20～1.70, P :≤0.018, S :≤0.008, Ti:0.008～0.03, Nb:0.02～0.05, Mo:0.2476～0.25, Cr :≤0.3, Als≤0.03, all the other are Fe and unavoidable impurities.
4. blast furnace hood steel, by the following chemical ingredients of forming by weight percentage ratio (%) be: C:0.05～0.12, Si:0.25～0.40, Mn:1.20～1.70, P :≤0.018, S :≤0.008, Ti:0.008～0.03, Nb:0.02～0.05, W:0.245～0.30, Mo:0.13～0.20, Cr :≤0.3, Als≤0.03, all the other are Fe and inevitable impurity.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100470092A CN101255534B (en) | 2008-03-06 | 2008-03-06 | Blast furnace hood steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100470092A CN101255534B (en) | 2008-03-06 | 2008-03-06 | Blast furnace hood steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101255534A CN101255534A (en) | 2008-09-03 |
| CN101255534B true CN101255534B (en) | 2011-04-20 |
Family
ID=39890627
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2008100470092A Expired - Fee Related CN101255534B (en) | 2008-03-06 | 2008-03-06 | Blast furnace hood steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101255534B (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1789468A (en) * | 2005-12-12 | 2006-06-21 | 上海梅山钢铁股份有限公司 | High-temperature creep resistant furnace shell material and preparation method thereof |
-
2008
- 2008-03-06 CN CN2008100470092A patent/CN101255534B/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1789468A (en) * | 2005-12-12 | 2006-06-21 | 上海梅山钢铁股份有限公司 | High-temperature creep resistant furnace shell material and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 戴连生,黄国祥.高炉炉壳用钢板的研制.武钢技术 3.1990,(3),2-6. |
| 戴连生,黄国祥.高炉炉壳用钢板的研制.武钢技术 3.1990,(3),2-6. * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101255534A (en) | 2008-09-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101368251B (en) | Steel plate for large-thickness hydrogen-contacting equipment and its production technology | |
| CN110241357B (en) | 800 MPa-grade tough weather-proof thick steel plate and preparation method thereof | |
| CN101451212B (en) | High intensity steel plate and preparation method thereof | |
| CN101748333B (en) | Low-carbon-equivalent high-strength wear-resistant steel plate and production method thereof | |
| CN102676945B (en) | Easily-weldable tempered high-strength ductile steel plate used in hydroelectric projects and production method thereof | |
| CN101451220A (en) | High-strength abrasion-proof steel plate and method for producing the same | |
| CN104532157A (en) | 900MPa-1000MPa grade (yield strength) quenched-tempered high-strength steel and production method thereof | |
| CN101451219A (en) | High intensity wear-resistant steel plate and preparation method thereof | |
| CN105543704A (en) | High-strength, shock-resistant, fire-proof and corrosion-proof steel plate and manufacturing method | |
| CN103526111A (en) | Hot-rolled plate band steel with yield strength being 900MPa and preparation method thereof | |
| CN109957712A (en) | Low-hardness X70M pipeline steel hot-rolled plate coil and manufacturing method thereof | |
| CN101096735A (en) | Easy-weld hardening high-strength steel plate and production method thereof | |
| CN108396240A (en) | Heat-resistant wear-resistant steel plate and production method thereof | |
| CN105063509A (en) | Structural steel with yield strength of 500 MPa for bridges and production method of structural steel | |
| CN103866203B (en) | A kind of heavy caliber high-strength bridge seamless steel pipe and TMCP production method thereof | |
| CN107130172B (en) | 400HBW grades of Brinell hardness whole constrictive type high tenacity easily weld special thick wear-resisting steel plate and its manufacturing method | |
| CN101328560A (en) | Ni seamless steel pipe and manufacturing method thereof | |
| CN110791714A (en) | 500MPa twisted steel with good welding performance and production method thereof | |
| CN114480806A (en) | Manufacturing method of thick TiC particle enhanced martensite wear-resistant steel plate | |
| CN102268602A (en) | 3Cr oil well pipe and production method thereof | |
| CN107287506A (en) | 650 MPa-level medium-temperature medium-pressure boiler steel plate and production method thereof | |
| CN101451221A (en) | High-strength steel plate and method for producing the same | |
| CN102127705B (en) | High-strength high-hardness wear-resistant steel | |
| CN102337458B (en) | Steel with tensile strength not lower than 1100MPa for engineering machinery and production method thereof | |
| CN106917051A (en) | A kind of corrosion-resistant two-phase wear-resisting steel plate and its production method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20110420 Termination date: 20170306 |