CN108286008A - A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof - Google Patents
A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof Download PDFInfo
- Publication number
- CN108286008A CN108286008A CN201810341054.2A CN201810341054A CN108286008A CN 108286008 A CN108286008 A CN 108286008A CN 201810341054 A CN201810341054 A CN 201810341054A CN 108286008 A CN108286008 A CN 108286008A
- Authority
- CN
- China
- Prior art keywords
- steel
- hot rolled
- low temperature
- shaped
- temperature 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
Classifications
-
- 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
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof, and chemical composition presses mass fraction：C：0.05~0.17%, Si：0.15~0.35%, Mn：1.0~2.0%, P：0.005~0.015%, S：0.005~0.015%, N：0.003~0.007%, O：0.002~0.005%, Ti：0.01~0.02%, Al：0.005~0.015%, Mg：0.001~0.005%, B：0.001~0.002%, Cr：0~0.5%, Mo：0~0.5%, surplus is Fe and impurity element, and Ti, Mg, O and N meet：2N≤Ti+1.3×Mg‑2×O≤4N；Method：1) molten iron and/or steel scrap are smelted into molten steel, carry out pre-deoxidation alloying and deep deoxidation；Then LF refining is carried out, micron-sized oxide is generated；Casting for shaped blank continuous；2) heating and thermal insulation；3) roughing and finish rolling are carried out；4) it is hot rolled H-shaped to obtain low temperature high-strength tenacity after cooling down；Its yield strength is 400~600MPa, 50 DEG C of impact flexibility >=100J.
Description
Technical field
The invention belongs to H profile steel production technical field, more particularly to a kind of low temperature high-strength tenacity is hot rolled H-shaped and its makes
Preparation Method.
Background technology
H profile steel is a kind of economic section high efficiency section bar, has that modulus of section is big, bending resistance is strong, construction is simple, saves steel
The advantages that material and lightweight construction, has been widely used in the industries such as building, bridge, ship, chemical industry.Hot rolled H-shaped and welding
Shaped steel reduces metal and energy consumption compared to that can save preparation section, improves production efficiency, therefore is most important H profile steel life
Production method.But since H profile steel cross sectional shape is special, rolling deformation carries out at a relatively high temperature, and passage deforms
Measure it is small, different parts deformation and non-uniform temperature be just more difficult to fully realize Unhydrated cement especially for think gauge shaped steel
Low temperature rolling improves for the uniform refinement and toughness and tenacity synthesis of tissue and brings difficulty.It is hot rolled H-shaped micro- to improve
Microstructure and mechanical property, people are explored and have been improved in terms of alloying component, smelting process, rolling and cooling technique.
It is special that patent document CN101925685A discloses a kind of toughness, the high-strength thick steel of excellent weldability and high intensity
The preparation method of thick h shape steel and they adds after dissolved oxygen is adjusted to 0.005~0.015wt.% by pre-deoxidation in smelting
Add Ti deoxidations, then carries out 30 minutes or more Fruit storages, form fine oxide containing Ti, pinning crystal boundary in steel
Thinning microstructure, to improve the toughness of special thicker steel.The above method need in advance by Oxygen Content in Liquid Steel be adjusted to a certain range it
It is interior, and need to be vacuum-treated, it is complicated for operation, bring the difficulty in production.
Patent document CN102418037A discloses a kind of hot rolled H-shaped and its preparation side with anti-lamellar tearing performance
Method, molten steel does not use Al deoxidations, and uses Si calmness deoxidations, at least one of Ti and Zr is then added, to be carried out to field trash
It is effectively rotten, improve steel Z-direction performance.But due to not using Al deep deoxidations, oxygen content in steel is higher, is easy to form large scale folder
Sundries reduces the cleanliness factor of steel.
Patent document CN102644020A discloses a kind of hot rolled H-shaped roller repairing of yield strength 500MPa level low alloys
Then method carries out two-part and is quickly cooled down to obtain carefully by Nb microalloyings and low temperature rolling fining austenite grains
The phase-change organization of change.In addition, patent document CN104831154A discloses a kind of H profile steel and its production method, using V microalloys
Change, carry out low temperature rolling, disclosure satisfy that -50 DEG C of low-temperature flexibility requirements.The above method uses addition Nb, V alloy element, and
Low temperature rolling is carried out, cost of alloy and mill load is increased, influences production efficiency.
In the technology of the current hot rolled H-shaped structure property of improvement, followed closely by forming fine oxide in smelting process
The method for pricking crystal grain implements means complexity, and is difficult to obtain best inclusion distribution, influences tissue thinning effect；And it adopts
With the method for addition alloy and zerolling, hence it is evident that production cost can be increased, and affected to equipment operation and production efficiency.
Therefore, it is necessary in view of the above-mentioned problems, carrying out hot rolled H-shaped production technology improvement and innovation, reduction production cost improves production effect
Rate, energy saving consumption significantly improve obdurability comprehensive mechanical property.
Invention content
In view of the deficiencies of the prior art, it is hot rolled H-shaped and preparation method thereof to provide a kind of low temperature high-strength tenacity by the present invention,
It solves the problems such as effective field trash is difficult to control, structure property ability of regulation and control is insufficient in H profile steel, is reducing cost of alloy, improving
Significantly improving for hot rolled H-shaped obdurability is realized under conditions of production efficiency.
A kind of low temperature is by mass fraction with the hot rolled H-shaped chemical composition of high-strength tenacity：C：0.05~0.17%, Si：
0.15~0.35%, Mn：1.0~2.0%, P：0.005~0.015%, S：0.005~0.015%, N：0.003~
0.007%, O：0.002~0.005%, Ti：0.01~0.02%, Al：0.005~0.015%, Mg：0.001~0.005%,
B：0.001~0.002%, Cr：0~0.5%, Mo：0~0.5%, surplus is Fe and impurity element, wherein Ti, Mg, O and N
Mass fraction meets relational expression：2N≤Ti+1.3×Mg-2×O≤4N.
The low temperature high-strength tenacity is hot rolled H-shaped, and the amount of inclusions that size is 0.2~5 μm in steel is ruler in steel
50 times or more of the very little the amount of inclusions for being more than 5 μm, size is 0.1~1 μm and contains MgAl in steel2O4The field trash of oxide
1000/mm of quantity ＞2, size is 0.3~3 μm and contains TiO in steelx500/the mm of the amount of inclusions ＞ of oxide2。
The low temperature high-strength tenacity is hot rolled H-shaped, yield strength be 400~600MPa, -50 DEG C of impact flexibility >=
100J, microscopic structure are Intragranular Acicular Ferrite and/or transgranular bainite type tissue.
A kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped, is as follows：
Step 1, it smelts：
(1) molten iron and/or steel scrap are smelted into molten steel, use Si and Mn to carry out pre-deoxidation alloying in tapping process,
Deep deoxidation is carried out using silico-calcium or Al；
(2) LF refining being carried out to molten steel after deoxidation, produces white slag in refining process, the white slag desulfurization retention time is 10~
20min；Al content is adjusted after desulfurization to 0.005~0.015wt.%, feeds Ti-Mg-O core-spun yarns, soft blow inert gas or nitrogen
10~20min of gas generates micron-sized oxide in molten steel；
(3) by the hot rolled H-shaped requirement accurate adjustment molten steel composition of low temperature high-strength tenacity, after refining, Hot Metal in Beam Blank is carried out
Continuous casting obtains continuous casting billet；
Step 2, it heats：
Continuous casting billet is heated to 1250~1300 DEG C, soaking time is 30~240min；
Step 3, it rolls：
Roughing and finish rolling are carried out to the continuous casting billet after heating, roughing start rolling temperature is 1200~1250 DEG C, the finish rolling finish to gauge wing
Edge temperature is 1050~1150 DEG C, 1000~1100 DEG C of web temperature, and H profile steel is made；
Step 4, cooling：
Roll rear H profile steel be cooled to the cooling rate of 1~10 DEG C/s it is air-cooled after 450 DEG C or less, or with the cooling rate of 5~20 DEG C/s
It is air-cooled again after being cooled to 570~670 DEG C, it is hot rolled H-shaped to obtain low temperature high-strength tenacity.
The hot rolled H-shaped preparation method of above-mentioned low temperature high-strength tenacity, wherein：
In the step 1, when raw material is steel scrap, using electric furnace smelting, when raw material is molten iron, using converter smelting,
When raw material is the mixture with steel scrap, using electric furnace or converter smelting.
In the step 1, steel scrap is non-alloyed or low-alloy steel scrap, Pb, As, Sb, Bi, Sn content summation ＜ in steel scrap
0.2wt.%, Cu, Ni, Cr, Mo content distinguish ＜ 0.5wt.%.
In the step 1, adjustment Al content is realized by adding aluminum shot, aluminum steel or aluminium powder.
In the step 1, LF refining carries out residue adjustment using aluminum shot, calcium carbide or ferrosilicon powder.
In the step 1, after deep deoxidation, dissolved oxygen is 1~10ppm in steel.
In the step 1, the Ti-Mg-O core-spun yarns of feeding are by titanium ferroally powder, Si-Mg alloy powder and brown iron oxide mixing
Filling is made, and wherein ferro-titanium accounts for 20~30wt.%, Si-Mg alloy accounts for 35~45wt.%, iron oxide accounts for 30~40wt.%,
150~200m/min of feeding speed, it is 20~60ppm to make molten steel total oxygen demand.
In the step 1, after LF refining, size is 5 μm or more of the amount of inclusions ＜ 10 in steel5A/cm3, LF terminals are molten
Oxygen is solved in 1~10ppm.
In the step 1, refining cycle is 50~70min.
In the step 1, refining feeds 100~300m calcium lines into molten steel after terminating and carries out Calcium treatment, soft blow after line feeding
6~15min of inert gas or nitrogen.
In the step 1, oxide contains the MgAl that size is 0.1~5 μm in molten steel after refining2O4、TiOxAnd the two
Composite oxides, and MgAl2O4、TiOxAnd the composite oxides quantity of the two accounts for 50% of oxide quantity or more.
In the step 3, roughing is carried out using roughing mill, finish rolling is carried out using universal finishing mill, the operation of rolling is needless to say warm
It is cooling.
The hot rolled H-shaped preparation method of above-mentioned low temperature high-strength tenacity, the design philosophy of technical solution are：
The difficult point that the present invention improves from hot rolled H-shaped production technology characteristic and toughness and tenacity, carries out ingredient decrement
Change design and the control of key component, using different from conventional structure property regulatory mechanism, passes through the collaboration of full process stream journey
It improves, had not only given full play to the production capacity of smelting and rolling process, but also the H profile steel product that availability is excellent.
This programme use relatively low C and medium Mn contents, using cheap element strengthen matrix, and ensure compared with low-carbon-equivalent with
Improve weldability；Utilize MgAl2O4、TiOxOxide plays pinning austenite grain and promotes the main of Intragranular Acicular Ferrite phase transformation
Effect, and predetermined size is in the quantitative proportion of 0.2~5 μm and 5 μm or more field trash, to play fine oxide to the thin of tissue
Change acts on, and avoids the adverse effect to matrix；When Ti, Mg, O, N meet required content range and relational expression 2N≤Ti+1.3
When × Mg-2 × O≤4N, best oxide and nitride distribution are can get, reduces adverse effect of the solid solution nitrogen to toughness,
And ensure the performance of boron element effect；Micro B is added and is remarkably improved bainite quenching degree, inhibits the generation of grain boundary ferrite,
Above-mentioned oxide is contributed to promote intergranular structure's transformation.It can be obtained under the conditions of H profile steel high temperature rolling using this programme component system
Microstructure, lead to peroxide induced Intragranular Acicular Ferrite forming core and realize refined crystalline strengthening and build up, at the same improve intensity and
Low-temperature flexibility realizes significantly improving for toughness and tenacity under conditions of not adding the precious alloys such as Nb, V.
To obtain above-mentioned effective oxide distribution in smelting process, it is complicated for method in current means, be not easy it is accurate
The problems such as control, this programme are being added Al deep deoxidations, are then feeding Ti-Mg-O core-spun yarns using Si and Mn pre-deoxidations are first added
Method, required oxide can be to easily and reliably generated in steel, and keep the structure composition of oxide more reasonable, point
Cloth is finer uniformly, and the effect of structure refinement is made to obtain performance to a greater extent.In rolling sequence, and generally use at present
The thinking of zerolling waits for temperature or cooling on the contrary, rolling sequence bulk temperature improves as possible in this programme, without centre, both protects
Rhythm of production has been held, and has reduced mill load and saves energy consumption, recrystallization or the non-recrystallization refinement of austenite has not been needed, only needs
The transgranular phase-change organization that can be obtained fine uniform structure under weaker water cooling condition, inhibits the formation of coarse friable tissues, and normal
The polygonal ferrite tissue for advising H profile steel is compared with more preferably toughness and tenacity.
A kind of low temperature high-strength tenacity of the present invention is hot rolled H-shaped and preparation method thereof, compared with prior art, advantage
And it has the beneficial effect that：
1, the component system of steel of the present invention is designed specifically for the production technology, is not required to the refined crystalline strengthenings such as addition Nb, V
With precipitation strength element, alloy low cost is, it can be achieved that H profile steel toughness and tenacity and the comprehensive of welding performance are improved.
2, the control method of oxide is simple and reliable in the present invention, and it is complicated, not easy to control to overcome method in routine techniques
The shortcomings that, and the composition of oxide and distribution are more reasonable under this programme technique, more preferably to the function and effect of structure refinement.
3, the present invention is deformed using high temperature rolling, is different from the thinking of common zerolling fining austenite grains, and
And needless to say temperature is cooling for the operation of rolling, reduces equipment energy consumption, improves production efficiency.
Even if 4, in minimizing component system and under the conditions of without zerolling, steel of the present invention still obtains microstructure, has both
High intensity and superior low-temperature toughness overcome the problem of generally hot rolled H-shaped production technology and performance improvement are difficult to coordinate and optimize.
Description of the drawings
Hot rolled H-shaped typical microstructures prepared by Fig. 1 embodiment of the present invention 3.
Specific implementation mode
The specific implementation mode of the present invention program is discussed in detail below by embodiment.
A kind of low temperature is by mass fraction with the hot rolled H-shaped chemical composition of high-strength tenacity：C：0.05~0.17%, Si：
0.15~0.35%, Mn：1.0~2.0%, P：0.005~0.015%, S：0.005~0.015%, N：0.003~
0.007%, O：0.002~0.005%, Ti：0.01~0.02%, Al：0.005~0.015%, Mg：0.001~0.005%,
B：0.001~0.002%, Cr：0~0.5%, Mo：0~0.5%, surplus is Fe and impurity element, wherein Ti, Mg, O and N
Mass fraction meets relational expression：2N≤Ti+1.3 × Mg-2 × O≤4N, each specific ingredient of embodiment are as shown in table 1.
A kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped, is as follows：
Step 1, it smelts：
(1) by molten iron by electro-smelting at molten steel, carry out pre-deoxidation alloying using Si and Mn in tapping process, use
Silico-calcium or A1 carry out deep deoxidation, and dissolved oxygen is as shown in table 3 in steel；
(2) LF refining is carried out to molten steel after deoxidation, white slag is produced using aluminum shot, calcium carbide or ferrosilicon powder in refining process,
The white slag desulfurization retention time is as shown in table 3；It is as shown in table 3 that Al content is adjusted after desulfurization, is fed by titanium ferroally powder, Si-Mg alloy
Ti-Mg-O core-spun yarns made of powder and the filling of brown iron oxide mixing, soft argon blowing time, molten steel total oxygen demand, refining cycle such as 3 institute of table
Show, the MgAl that size is 0.1~5 μm is generated in molten steel2O4、TiOxAnd the composite oxides of the two, make in each embodiment steel
Inclusion distribution is as shown in table 2；
(3) by the hot rolled H-shaped requirement accurate adjustment molten steel composition of low temperature high-strength tenacity, specific ingredient is as shown in table 1, refining
After, LF terminal dissolved oxygens are as shown in table 3, carry out casting for shaped blank continuous, obtain continuous casting billet；
Step 2, it heats：
Continuous casting billet is heated and kept the temperature, design parameter is as shown in table 4；
Step 3, it rolls：
Roughing is carried out using roughing mill to the continuous casting billet after heating, finish rolling is carried out using universal finishing mill, the operation of rolling is not
It waits for warm cooling, H profile steel is made, roughing start rolling temperature, finish rolling finish to gauge edge of a wing temperature, web temperature are as shown in table 4；
Step 4, cooling：
Rear H profile steel is rolled by air-cooled after water cooling, and it is hot rolled H-shaped to obtain low temperature high-strength tenacity, cooling velocity and cold eventually
Temperature is as shown in table 4.
The chemical composition (wt.%) of 1 various embodiments of the present invention of table
Inclusion distribution feature in 2 each embodiment of table
The smelting parameter of 3 each embodiment of table
The rolling technological parameter of 4 each embodiment of table
Low temperature high-strength tenacity prepared by the present invention is hot rolled H-shaped, yield strength, -50 DEG C of impact flexibility such as 5 institute of table
Show, microscopic structure is Intragranular Acicular Ferrite and/or transgranular bainite type tissue, can meet the performance requirement of low temperature structure steel.
As shown in Figure 1, the microscopic structure of H profile steel prepared by embodiment 3 and conventional hot rolled H-shaped polygonal ferrite tissue
Difference belongs to Intragranular Acicular Ferrite and bainite type tissue, and crystallite dimension refinement is uniform, conducive to significantly improving for obdurability.
The mechanical property of 5 each embodiment of table
| Embodiment | Yield strength/MPa | Impact flexibility/J (- 50 DEG C) |
| 1 | 510 | 160 |
| 2 | 525 | 155 |
| 3 | 450 | 208 |
| 4 | 443 | 210 |
| 5 | 585 | 120 |
| 6 | 570 | 135 |
Claims (10)
1. a kind of low temperature high-strength tenacity is hot rolled H-shaped, which is characterized in that the chemical composition of steel is by mass fraction：C：0.05
~0.17%, Si：0.15~0.35%, Mn：1.0~2.0%, P：0.005~0.015%, S：0.005~0.015%, N：
0.003~0.007%, O：0.002~0.005%, Ti：0.01~0.02%, Al：0.005~0.015%, Mg：0.001~
0.005%, B：0.001~0.002%, Cr：0~0.5%, Mo：0~0.5%, surplus be Fe and impurity element, wherein Ti,
The mass fraction of Mg, O and N meet relational expression：2N≤Ti+1.3×Mg-2×O≤4N；
The low temperature high-strength tenacity is hot rolled H-shaped, and the amount of inclusions that size is 0.2~5 μm in steel is that size is big in steel
In 50 times or more of 5 μm of the amount of inclusions, size is 0.1~1 μm and contains MgAl in steel2O4The amount of inclusions of oxide
1000/mm of ＞2, size is 0.3~3 μm and contains TiO in steelx500/the mm of the amount of inclusions ＞ of oxide2。
2. a kind of low temperature high-strength tenacity according to claim 1 is hot rolled H-shaped, which is characterized in that the H profile steel is bent
It is 400~600MPa to take intensity, and -50 DEG C of impact flexibility >=100J, microscopic structure is Intragranular Acicular Ferrite and/or transgranular bainite type
Tissue.
3. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped described in claim 1, which is characterized in that specific step
It is rapid as follows：
Step 1, it smelts：
(1) molten iron and/or steel scrap are smelted into molten steel, Si and Mn progress pre-deoxidation alloyings, use is used in tapping process
Silico-calcium or Al carry out deep deoxidation；
(2) LF refining is carried out to molten steel after deoxidation, white slag is produced in refining process, the white slag desulfurization retention time is 10~20min；
Al content is adjusted after desulfurization to 0.005~0.015wt.%, feeds Ti-Mg-O core-spun yarns, soft blow inert gas or nitrogen 10~
20min generates micron-sized oxide in molten steel；
(3) by the hot rolled H-shaped requirement accurate adjustment molten steel composition of low temperature high-strength tenacity, after refining, casting for shaped blank continuous is carried out,
Obtain continuous casting billet；
Step 2, it heats：
Continuous casting billet is heated to 1250~1300 DEG C, soaking time is 30~240min；
Step 3, it rolls：
Roughing and finish rolling are carried out to the continuous casting billet after heating, roughing start rolling temperature is 1200~1250 DEG C, finish rolling finish to gauge edge of a wing temperature
Degree is 1050~1150 DEG C, 1000~1100 DEG C of web temperature, and H profile steel is made；
Step 4, cooling：
It rolls rear H profile steel and is cooled to the cooling rate of 1~10 DEG C/s air-cooled after 450 DEG C or less, or cooled down with the cooling rate of 5~20 DEG C/s
It is air-cooled again after to 570~670 DEG C, it is hot rolled H-shaped to obtain low temperature high-strength tenacity.
4. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
It states in step 1, steel scrap is non-alloyed or low-alloy steel scrap, Pb, As, Sb, Bi, Sn content summation ＜ 0.2wt.%, Cu in steel scrap,
Ni, Cr, Mo content distinguish ＜ 0.5wt.%.
5. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
It states in step 1, LF refining carries out residue adjustment using aluminum shot, calcium carbide or ferrosilicon powder.
6. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
It states in step 1, after deep deoxidation, dissolved oxygen is 1~10ppm in steel.
7. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
It states in step 1, the Ti-Mg-O core-spun yarns of feeding are made of the filling of titanium ferroally powder, Si-Mg alloy powder and brown iron oxide mixing,
Middle ferro-titanium accounts for 20~30wt.%, Si-Mg alloy accounts for 35~45wt.%, iron oxide accounts for 30~40wt.%, feeding speed 150
~200m/min, it is 20~60ppm to make molten steel total oxygen demand.
8. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
It states in step 1, after LF refining, size is 5 μm or more of the amount of inclusions ＜ 10 in steel5A/cm3, LF terminals dissolved oxygen 1~
10ppm。
9. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
It states in step 1, oxide contains the MgAl that size is 0.1~5 μm in molten steel after refining2O4、TiOxAnd the combined oxidation of the two
Object, and MgAl2O4、TiOxAnd the composite oxides quantity of the two accounts for 50% of oxide quantity or more.
10. a kind of preparation method that low temperature high-strength tenacity is hot rolled H-shaped according to claim 3, which is characterized in that institute
State in step 1, refining terminate after into molten steel feed 100~300m calcium lines carry out Calcium treatment, after line feeding soft blow inert gas or
6~15min of nitrogen.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810341054.2A CN108286008B (en) | 2018-04-17 | 2018-04-17 | A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810341054.2A CN108286008B (en) | 2018-04-17 | 2018-04-17 | A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN108286008A true CN108286008A (en) | 2018-07-17 |
| CN108286008B CN108286008B (en) | 2019-10-01 |
Family
ID=62834588
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810341054.2A Active CN108286008B (en) | 2018-04-17 | 2018-04-17 | A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN108286008B (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109338040A (en) * | 2018-11-15 | 2019-02-15 | 包头钢铁（集团）有限责任公司 | A kind of large size boracic SS275 is hot rolled H-shaped and its production method |
| CN109338227A (en) * | 2018-11-21 | 2019-02-15 | 包头钢铁（集团）有限责任公司 | Low temperature resistant H profile steel of a kind of 275MPa grades of boracic hot rolling and preparation method thereof |
| CN109797343A (en) * | 2019-01-22 | 2019-05-24 | 山东钢铁股份有限公司 | A kind of low-alloy high-strength hot strip rolling and preparation method thereof suitable for extremely cold area |
| CN110079728A (en) * | 2019-04-09 | 2019-08-02 | 东北大学 | A kind of good high-strength deformed steel bar muscle of weldability and its manufacturing method |
| CN110144522A (en) * | 2019-06-04 | 2019-08-20 | 河北科技大学 | A kind of oxide fine grain type spiral and its production technology |
| CN110527896A (en) * | 2019-09-23 | 2019-12-03 | 江苏方圆型钢有限公司 | A kind of hot-rolled steel section and its production technology |
| CN111574118A (en) * | 2020-05-16 | 2020-08-25 | 深圳市绿悦环保科技有限公司 | Construction waste recycling method |
| CN112267005A (en) * | 2020-09-23 | 2021-01-26 | 舞阳钢铁有限责任公司 | Steel-making method for welding steel plate with large heat input |
| CN113025904A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Hot-rolled seamless steel pipe and deformation and phase change integrated structure regulation and control method thereof |
| CN113025903A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Fine-grain hot-rolled plate strip steel and preparation method thereof |
| CN115418559A (en) * | 2022-07-20 | 2022-12-02 | 山东钢铁股份有限公司 | High-strength and high-toughness hot-rolled H-shaped steel for buildings and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004019001A (en) * | 2002-06-20 | 2004-01-22 | Daido Steel Co Ltd | Tool steel for hot-working superior in erosion resistance, and die member |
| CN105525213A (en) * | 2016-01-21 | 2016-04-27 | 东北大学 | High-strength-toughness and high-temperature hot rolled steel plate and preparation method thereof |
-
2018
- 2018-04-17 CN CN201810341054.2A patent/CN108286008B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004019001A (en) * | 2002-06-20 | 2004-01-22 | Daido Steel Co Ltd | Tool steel for hot-working superior in erosion resistance, and die member |
| CN105525213A (en) * | 2016-01-21 | 2016-04-27 | 东北大学 | High-strength-toughness and high-temperature hot rolled steel plate and preparation method thereof |
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109338040A (en) * | 2018-11-15 | 2019-02-15 | 包头钢铁（集团）有限责任公司 | A kind of large size boracic SS275 is hot rolled H-shaped and its production method |
| CN109338227A (en) * | 2018-11-21 | 2019-02-15 | 包头钢铁（集团）有限责任公司 | Low temperature resistant H profile steel of a kind of 275MPa grades of boracic hot rolling and preparation method thereof |
| CN109797343A (en) * | 2019-01-22 | 2019-05-24 | 山东钢铁股份有限公司 | A kind of low-alloy high-strength hot strip rolling and preparation method thereof suitable for extremely cold area |
| CN110079728A (en) * | 2019-04-09 | 2019-08-02 | 东北大学 | A kind of good high-strength deformed steel bar muscle of weldability and its manufacturing method |
| WO2020206744A1 (en) * | 2019-04-09 | 2020-10-15 | 东北大学 | High-strength ribbed reinforcing bar having good weldability, and manufacturing method therefor |
| CN110144522A (en) * | 2019-06-04 | 2019-08-20 | 河北科技大学 | A kind of oxide fine grain type spiral and its production technology |
| CN110527896B (en) * | 2019-09-23 | 2021-06-25 | 江苏方圆型钢有限公司 | Hot-rolled section steel and production process thereof |
| CN110527896A (en) * | 2019-09-23 | 2019-12-03 | 江苏方圆型钢有限公司 | A kind of hot-rolled steel section and its production technology |
| CN111574118A (en) * | 2020-05-16 | 2020-08-25 | 深圳市绿悦环保科技有限公司 | Construction waste recycling method |
| CN112267005A (en) * | 2020-09-23 | 2021-01-26 | 舞阳钢铁有限责任公司 | Steel-making method for welding steel plate with large heat input |
| CN113025904A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Hot-rolled seamless steel pipe and deformation and phase change integrated structure regulation and control method thereof |
| CN113025903A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Fine-grain hot-rolled plate strip steel and preparation method thereof |
| CN113025904B (en) * | 2021-03-04 | 2022-02-01 | 东北大学 | Hot-rolled seamless steel pipe and deformation and phase change integrated structure regulation and control method thereof |
| CN114086069A (en) * | 2021-03-04 | 2022-02-25 | 东北大学 | Magnesium-containing fine-grain hot-rolled plate strip steel and preparation method thereof |
| CN115418559A (en) * | 2022-07-20 | 2022-12-02 | 山东钢铁股份有限公司 | High-strength and high-toughness hot-rolled H-shaped steel for buildings and preparation method thereof |
| CN115418559B (en) * | 2022-07-20 | 2023-11-07 | 山东钢铁股份有限公司 | High-strength and high-toughness hot rolled H-shaped steel for building and preparation method thereof |
| WO2024016543A1 (en) * | 2022-07-20 | 2024-01-25 | 山东钢铁股份有限公司 | High-strength and high-toughness hot-rolled h-shaped steel for building and preparation method therefor |
Also Published As
| Publication number | Publication date |
|---|---|
| CN108286008B (en) | 2019-10-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108286008B (en) | A kind of low temperature high-strength tenacity is hot rolled H-shaped and preparation method thereof | |
| CN101153370B (en) | Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same | |
| CN108374126B (en) | A kind of high intensity fine grain reinforcing bar and preparation method thereof | |
| CN106987771B (en) | A kind of extremely low yield strength steel plate and its production method | |
| CN108531806B (en) | A kind of high-strength tenacity hot rolled seamless steel tube and preparation method thereof | |
| CN103305746B (en) | The high-strength steel band manufacture method of a kind of age hardening thin strap continuous casting low-carbon microalloy | |
| CN110042303A (en) | A kind of 400MPa grades of fine grain hot-rolled reinforcing bar and its production technology | |
| CN110257719A (en) | A kind of micro-alloyed with Nb and Ti HRB400 grades of screw-thread steels and its manufacturing method | |
| CN109385576A (en) | A kind of inexpensive X65 pipe line steel and its manufacturing method based on magnesium processing | |
| CN103215516A (en) | 700MPa high strength hot rolling Q&P steel and manufacturing method thereof | |
| CN109930056A (en) | A kind of 400MPa grades of fine grain spiral and its manufacturing method | |
| CN106167875A (en) | A kind of strength and ductility product economical high strength cold-rolled TRIP steel more than 20GPa % and preparation method thereof | |
| CN107964624A (en) | A kind of yield strength 500MPa level structure steel and preparation method thereof | |
| CN106811684B (en) | 750Mpa grades of container hot rolled steel plates of yield strength and its manufacturing method | |
| CN102199732B (en) | Boron containing steel plate for heat treatment and manufacturing method thereof | |
| CN108588550A (en) | A kind of hot rolling press axle housing steel plate and its production method | |
| CN102605241A (en) | Normalizing type 16MnDR low temperature pressure vessel steel plate and manufacturing method thereof | |
| CN107779740B (en) | Yield strength 700MPa grade atmospheric corrosion resistant hot rolled strip and manufacturing method | |
| CN113846260B (en) | Production method of high-strength steel plate for engineering machinery | |
| CN108796370A (en) | A kind of the welding structure fire-resistant and weather-resistant steel and its production method of yield strength >=690MPa | |
| CN107190203A (en) | With the yield strength >=800MPa SPHCs and production method of sheet billet Direct Rolling | |
| CN106435384A (en) | Vanadium-containing automobile structural steel and production method thereof | |
| CN102400045B (en) | Large-specification and high-strength D40 hot-rolled flat-bulb steel for ships and production process for hot-rolled flat-bulb steel | |
| CN110144522A (en) | A kind of oxide fine grain type spiral and its production technology | |
| CN106244926A (en) | A kind of containing vanadium steel used for vehicle transmission shaft and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |