A 460 MPa-grade extra-thick hot-rolled H-shaped steel and a production method therefor. The 460 MPa-grade extra-thick hot-rolled H-shaped steel comprises components C: 0.10-0.20%, Si: 0.30-0.50%, Mn: 0.8% -1.50%, P ≤ 0.015%, S ≤ 0.005%, Nb: 0.010-0.050%, V: 0.040% -0.100%, Ti: 0.006% -0.020%, Cr: 0.10% -0.30%, N: 0.0060% -0.0120%, and the balance of Fe and inevitable impurities, 0.35% ≤ C+Mn/6 ≤ 0.45%, and 0.060% ≤ Nb+V ≤ 0.130%. In production, after blanks are continuously cast, a blank slow cooling area is provided so as to slowly cool a pull-out blank pile by means of a specific process, and subsequently controlled rolling and controlled cooling are carried out, thereby solving difficulties in producing extra-thick high-strength hot-rolled H-shaped steel, and allowing for low components and excellent performance.
A production method for improving the Z-direction performance of heavy hot-rolled H-section steel, and a heavy hot-rolled H-section steel. The production method comprises the following steps: molten iron pretreatment, converter double-slag smelting, LF furnace refining, VD vacuum degassing, continuous casting, slow cooling, hot rolling, and cooling. In the step of continuous casting, low-superheat, constant-drawing speed casting is used, superheat being 10-35°C, and the continuous casting drawing speed of a profiled billet section being 0.45-0.95 m/min; the secondary cooling water ratio is 0.45-0.77 L/kg, the foot roller area is cooled by water, and the active section, the first section, the second section and the third section are cooled by air-water atomization; the water distribution ratio of the foot roller area, the active section, the first section, the second section and the third section is 25-33%:40-45%:15-20%:7-10%:4.5-6%; the Z-direction performance of the produced heavy hot-rolled H-shaped steel is 35-65%, and the cast billet surface quality is good.
11122233344422 ≥ 80 J, and a contact fatigue life ≥ 1 million times under the action of a contact stress of 2,000 MPa, which satisfy the requirements for 20-year service for high-power wind power.
C22C 38/20 - Ferrous alloys, e.g. steel alloys containing chromium with copper
C22C 38/24 - Ferrous alloys, e.g. steel alloys containing chromium with vanadium
C22C 38/26 - Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
C22C 38/02 - Ferrous alloys, e.g. steel alloys containing silicon
C22C 38/04 - Ferrous alloys, e.g. steel alloys containing manganese
C22C 38/06 - Ferrous alloys, e.g. steel alloys containing aluminium
C21D 1/25 - Hardening, combined with annealing between 300 °C and 600 °C, i.e. heat refining ("Vergüten")
C21D 9/40 - Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor for ringsHeat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor for bearing races
4.
Extra thick hot rolled h section steel and production method therefor
The present invention discloses a extra thick hot rolled H section steel and a production method therefor. The extra thick hot rolled H section steel contains, by mass, the following chemical components: 0.04-0.11% of C, 0.10-0.40% of Si, 0.40-1.00% of Mn, 0.40-1.00% of Cr, 0.10-0.40% of Cu, 0.020-0.060% of Nb, 0.040-0.100% of V, 0.010-0.025% of Ti, 0.010-0.030% of Al, 0.0060-0.0120% of N, not more than 0.015% of P, not more than 0.005% of S, not more than 0.0060% of O, and the balance Fe and trace residual elements, wherein 0.090%≤Nb+V+Ti≤0.170%, 6.5≤(V+Ti)/N≤10.5, and 0.30%≤CEV≤0.48%. The extra thick hot rolled H section steel has a flange thickness of 90 mm-150 mm, has excellent comprehensive mechanical properties, and can well meet the needs for heavy supporting structural parts of high-rise buildings, large squares, bridge structures, etc.
A low-silicon Nb-V composite microalloyed gear steel and a manufacturing method therefor, which belong to the technical field of gear steels. A gear steel comprises the following chemical components in percentages by weight: C: 0.22-0.26%, Si: ≤0.10%, Mn: 0.30-0.50%, Cr: 0.70-0.90%, Mo: 0.30-0.50%, Ni: 0.30-0.50%, Al: 0.030-0.050%, Nb: 0.030-0.060%, V: 0.10-0.50%; P: ≤0.010%, S: ≤0.015%, T.O: ≤10 ppm, and [N]: 60-120 ppm, with the balance being Fe and inevitable impurities. The depth of a surface oxidation layer during a gear carburizing process is effectively reduced by means of element matching and process optimization, and the obtained gear steel has a tensile strength of 1050-1200 MPa, a yield strength of 840-950 MPa, a percentage elongation after fracture of ≥30%, the percentage reduction of area of ≥40%, a room-temperature impact energy (U2) of ≥85 J, an oxidation layer depth after carburizing of ≤35 μm, and a rotating bending fatigue strength of ≥680 MPa.
C22C 38/48 - Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
C22C 38/46 - Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
C22C 38/44 - Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
C22C 38/06 - Ferrous alloys, e.g. steel alloys containing aluminium
C22C 38/04 - Ferrous alloys, e.g. steel alloys containing manganese
C22C 38/02 - Ferrous alloys, e.g. steel alloys containing silicon
C21D 1/18 - HardeningQuenching with or without subsequent tempering
C22C 33/06 - Making ferrous alloys by melting using master alloys
C23C 8/00 - Solid state diffusion of only non-metal elements into metallic material surfacesChemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
6.
STEEL FOR HIGH-TOUGHNESS CORROSION-RESISTANT CHRISTMAS TREE VALVE BODIES SMELTED AT HIGH SCRAP RATIO, AND HEAT TREATMENT METHOD AND PRODUCTION METHOD THEREFOR
22 greater than or equal to 220 J at -46°C, A greater than or equal to 20%, Z greater than or equal to 70%, and a corrosion rate in the seawater environment less than or equal to 0.09 mm/a, and the performance thereof satisfies the requirements of a Christmas tree in a harsh environment.
C21D 1/18 - HardeningQuenching with or without subsequent tempering
7.
HIGH-STRENGTH AND HIGH-TOUGHNESS STEEL WITH LONG SERVICE LIFE AND WALL THICKNESS OF ≥ 600 MM FOR VALVE BODY OF SUBSEA CHRISTMAS TREE, AND HEAT TREATMENT METHOD AND PRODUCTION METHOD THEREFOR
High-strength and high-toughness steel with a long service life and a wall thickness of ≥ 600 mm for a valve body of a subsea Christmas tree, and a heat treatment method and production method therefor. The steel for a valve body of a subsea Christmas tree mainly comprises the following components: C, Si, Mn, Cr, Mo, Ni, Cu, Al, Nb, Ti, B and N, wherein {2.5+30×[B-1.27×(N-0.002-0.29×Ti-0.15×Nb)]}×(1+4×Mn)×(1+2×Cr)×(1+3.5×Mo) ≥ 90; and 30×Ni+20×Mo+16×Cu+22×Mn-12×Si×Mn+28×C-10×C×Mn ≥ 74.5. By controlling the composition and amounts of the chemical components of the steel, the performance of the steel can meet the requirements of a subsea Christmas tree in a harsh environment, and the fatigue strength of the steel is ≥ 320 MPa after the steel is corroded for 2×107 cycles in a seawater environment.
LONG-SERVICE-LIFE HIGH-TOUGHNESS CORROSION-RESISTANT STEEL FOR SUBSEA CHRISTMAS TREE VALVE AND HEAT TREATMENT METHOD AND PRODUCTION METHOD FOR LONG-SERVICE-LIFE HIGH-TOUGHNESS CORROSION-RESISTANT STEEL FOR SUBSEA CHRISTMAS TREE VALVE
Long-service-life high-toughness corrosion-resistant steel for a subsea Christmas tree valve and a heat treatment method and production method for the long-service-life high-toughness corrosion-resistant steel for the subsea Christmas tree valve. The steel for the subsea Christmas tree valve mainly comprises the following components: C, Si, Mn, Cr, Mo, Ni, Cu, and Al. The compositions of the chemical components of the steel and the relationships and contents of the components are controlled, such that the tensile strength at the 1/4 thickness of the steel valve for the subsea Christmas tree valve is greater than or equal to 860 MPa, the yield strength is greater than or equal to 690 MPa, KV2 at -46°C is greater than or equal to 230 J, A is greater than or equal to 20%, and Z is greater than or equal to 70%; the corrosion rate in a seawater environment is less than or equal to 0.07 mm/a; the fatigue strength is greater than or equal to 350 MPa after 2*107 weeks of corrosion in a seawater environment; and the performance of the steel can meet the requirements of a subsea Christmas tree in a severe environment.
Disclosed in the present invention are heavy hot-rolled H section steel with Z-direction performance and a production method therefor. The hot-rolled H section steel comprises the following chemical components: C, Si, Mn, Nb, Ti, N, B, Als, and the balance of iron and inevitable impurities. The production method comprises the following steps: molten iron pretreatment→converter smelting→argon blowing refining→RH→full-protection pouring of a special-shaped blank→stacking for slow cooling→air cooling after rolling. In the present invention, by means of reasonable component proportioning and process control, the process of cogging rolling+universal rolling+air cooling after rolling, and the mode of combined phase change, precipitation and fine grain strengthening, the precipitation quantity of second-direction particles is regulated and controlled, and the content of obtained rolled granular bainite is between 10% and 20%, such that the heavy hot-rolled H section steel with the flange thickness of 80 mm or less has an excellent toughness and Z-direction performance, and the Z-direction performance is 65-80%.
B21B 45/02 - Devices for surface treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
10.
HOT-ROLLED H-SHAPED STEEL AND PRODUCTION METHOD THEREFOR
Disclosed in the present invention is hot-rolled H-shaped steel, which comprises a web plate, a first flange plate and a second flange plate, wherein a thickness difference |T1-T2| between the first flange plate and the second flange plate is greater than 0, the ratio of an area difference |S1-S2| between the first flange plate and the second flange plate to an area S1 of the first flange plate is not greater than 1, or the ratio of the area difference |S1-S2| between the first flange plate and the second flange plate to an area S2 of the second flange plate is not greater than 1. The hot-rolled H-shaped steel of the present invention can satisfy the production requirements of different thicknesses of flanges of various specifications on two sides, and can also prevent lateral bending in a rolling process, and the difference of metal flow per second of the flanges on two sides in the rolling process is controlled within a certain range, such that the hot-rolled H-shaped steel with different thicknesses of flanges on two sides is stably produced. Further disclosed in the present invention is a production method for the hot-rolled H-shaped steel.
B21B 1/08 - Metal rolling methods or mills for making semi-finished products of solid or profiled cross-sectionSequence of operations in milling trainsLayout of rolling-mill plant, e.g. grouping of standsSuccession of passes or of sectional pass alternations for rolling work of special cross-section, e.g. angle steel
B21B 1/46 - Metal rolling methods or mills for making semi-finished products of solid or profiled cross-sectionSequence of operations in milling trainsLayout of rolling-mill plant, e.g. grouping of standsSuccession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
B21B 37/00 - Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
11.
PRE-COATED STEEL PLATE FOR HOT FORMING AND PREPARATION METHOD THEREFOR, AND HOT-FORMED STEEL MEMBER AND APPLICATION THEREOF
Disclosed in the present invention are a pre-coated steel plate for hot forming and a preparation method therefor, and a hot-formed steel member and an application thereof. In the pre-coated steel plate and the preparation method therefor, when the thickness of a pre-coating is 5-19 μm, the corresponding surface roughness of the pre-coating is set, a hot-formed coated steel member can be obtained after hot forming, and the coating on the hot-formed coated steel member has a high surface roughness of Ra≥1.80 μm; the obtained steel member has the advantages of light weight, high surface roughness and good paint adhesion and paint corrosion resistance, and a steel part made of the steel member of the present invention can be applied to a vehicle so as to lighten the weight of the vehicle.
Disclosed in the present invention are a hot-formed steel having a blue or light blue aluminum alloy plating layer, a hot forming process, and a hot-formed part. A thermal treatment method comprises the following steps: performing optical finishing and tension leveling on a substrate subsequent to hot dipping plating; and then performing heating by means of a heating furnace at 900-930°C, and discharging from the furnace and transferring to a mold for flat plate quenching. An aluminum-silicon plated hot-formed steel having a blue or light blue surface can be produced according to the method; a high-strength aluminum-silicon plated hot-formed steel having the blue or light blue surface can be obtained by using the thermal treatment method of the present invention to treat a steel plate having a specific substrate component; and the present invention produces a 1,500 MPa grade hot-formed steel having the blue or light blue surface and a 1,800 MPa grade hot-formed steel having the blue or light blue surface, and the hot-formed steel can be widely applied to automobile structural members, reinforcing members, and anti-collision members.
Disclosed are a top hat steel rolling method and a top hat steel. The process flow of the present rolling comprises: heating → high-pressure water descaling → cogging and blank rolling → reciprocating continuous rolling → cooling → straightening. Rolling hole shapes comprise a wavy flat arc-shaped pre-cut split hole, an M-shaped top hat-typed split hole, a top hat-typed finish rolling hole, and a hot-rolled finished hole. The middle portion of the top hat-typed finish rolling hole and the hot-rolled finished hole has an arc-shaped section. An upper leg portion and a lower leg portion are symmetrically provided at two ends of the arc-shaped section. An included angle is formed between the upper end of the upper leg portion and one end of the arc-shaped section. The lower leg portion is arranged at a lower end of the side of the upper leg portion away from the arc-shaped section, and the lower leg portion intersects with the upper leg portion to form an included angle. The top hat steel comprises a horizontal waist portion, two ends of which are respectively symmetrically provided with vertically placed vertical legs and horizontally placed horizontal legs, and the horizontal legs are positioned on the side of the vertical legs away from the waist portion. The present invention may effectively improve the production efficiency of top hat steel, improve rolling stability, reduce process design difficulty, and reduce roller equipment loss.
B21B 1/08 - Metal rolling methods or mills for making semi-finished products of solid or profiled cross-sectionSequence of operations in milling trainsLayout of rolling-mill plant, e.g. grouping of standsSuccession of passes or of sectional pass alternations for rolling work of special cross-section, e.g. angle steel
B21B 37/16 - Control of thickness, width, diameter or other transverse dimensions
Disclosed in the present invention are a super-thick-gauge hot rolled H-beam and a production method therefor, the chemical components thereof comprising in mass percentage: C: 0.04-0.11, Si: 0.10-0.40, Mn: 0.40-1.00, Cr: 0.40-1.00, Cu: 0.10-0.40, Nb: 0.020-0.060, V: 0.040-0.100, Ti: 0.010-0.025, Al: 0.010-0.030, N: 0.0060-0.0120, P: ≤0.015, S: ≤0.005, O: ≤0.0060, 0.090%≤Nb+V+Ti≤0.170%, 6.5≤(V+Ti)/N≤10.5, the remainder being Fe and trace residual elements, 0.30%≤CEV≤0.48%; the present invention has a flange thickness of 90 mm to 150 mm and excellent comprehensive mechanical properties, and can well satisfy the requirements of heavy supporting structural parts of high-rise buildings, large squares, and bridge structures.
Provided are a -165°C-low-temperature-resistant rebar mechanical connection coupler for an LNG storage tank and a production method therefor. The production method involves: subjecting a coupler parent material to inner and outer circle turning → processing a female thread using a tapping machine → quenching → tempering process to prepare the coupler, wherein the components of the parent material include: 0.06-0.12% of C, 0.30-0.50% of Si, 1.30-1.80% of Mn, 1.00-2.50% of Ni, 0.060-1.000% of V, P ≤ 0.010%, S ≤ 0.010%, H ≤ 0.00015%, and O ≤ 0.0015%, with the balance being Fe and impurity elements. The mechanical connection coupler of the present invention is produced using a grade of steel different from the prior art, and the production method is controlled. The produced coupler can satisfy the -165°C-low-temperature resistance requirement for rebar-reinforced concrete structures of LNG, etc., low-temperature storage tanks in China.
The present invention provides a high strength, high toughness, heat-cracking resistant bainite steel wheel for rail transportation and a manufacturing method thereof. Components are: carbon 0.10-0.40%, silicon 1.00-2.00%, manganese 1.00-2.50%, copper 0.20-1.00%, boron 0.0001-0.035%, nickel 0.10-1.00%, phosphorus ≤0.020%, and sulphur ≤0.020%, where the remaining is iron and unavoidable residual elements, 1.50%≤Si+Ni≤3.00%, and 1.50%≤Mn+Ni+Cu≤3.00%. Compared with the prior art, in the present invention, by using design of the chemical compositions of steel and wheel manufacturing processes, especially a heat treatment process and technology, a rim of the wheel obtains a carbide-free bainite structure, and a web and a wheel hub obtain a metallographic structure based on granular bainite and a supersaturated ferritic structure. The wheel has comprehensive mechanical properties such as high strength, high toughness, heat-cracking resistant performance and good service performance, thereby improving a service life and comprehensive efficiency of the wheel, bringing specific economic and social benefits.
C22C 38/16 - Ferrous alloys, e.g. steel alloys containing copper
C21D 9/34 - Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor for tyresHeat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor for rims
C21D 1/18 - HardeningQuenching with or without subsequent tempering
C21D 9/00 - Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor
C22C 38/02 - Ferrous alloys, e.g. steel alloys containing silicon
C22C 38/04 - Ferrous alloys, e.g. steel alloys containing manganese
C22C 38/08 - Ferrous alloys, e.g. steel alloys containing nickel
17.
CONTINUOUS CASTING SOLIDIFICATION PROCESS CONTROL METHOD FOR INHIBITING GROWTH OF COLUMNAR CRYSTALS
A continuous casting solidification process control method for inhibiting growth of columnar crystals comprises applying an intermittent excitation force to a surface of a solidified ingot shell of a continuously cast ingot, wherein a metal liquid phase ratio in a cross section of the cast ingot at a point where the excitation force is applied is 25%-85%. The excitation force striking the ingot shell on the surface of the cast ingot breaks dendritic crystal heads growing at a solidification front edge during a cooling process, promotes conversion of columnar crystals into equiaxed crystals, does not increase continuous relative displacement between molten steel and dendritic crystals at the solidified front edge caused by an external field force, and inhibits transfer of a solute element in steel to the molten steel, thereby inhibiting growth of the columnar crystals, promoting growth of equiaxed crystals, and eliminating or reducing negative segregation of the cast ingot.
B22D 11/114 - Treating the molten metal by using agitating or vibrating means
B22D 11/16 - Controlling or regulating processes or operations
18.
METHOD FOR IMPROVING FLUIDITY OF SOLID-LIQUID TWO-PHASE REGION IN MIDDLE AND LATE SOLIDIFICATION STAGES OF CONTINUOUS CASTING PROCESS, AND METHOD AND DEVICE FOR CONTROLLING QUALITY OF CAST INGOT
A method for improving the fluidity of a solid-liquid two-phase region in middle and late solidification stages of a continuous casting process comprises applying intermittent excitation force to a surface of an ingot shell (120) at a solidified end of a continuously cast ingot (100), wherein intermittent excitation force can be further applied to the surface of the ingot shell at a solidified intermediate segment of the continuously cast ingot. Additionally, a method for controlling quality of a cast ingot in a solidification process of continuous casting and a device for controlling quality of a cast ingot in a solidification process of continuous casting are provided. Excitation force applied to a surface of an ingot shell at a solidified end of a continuously cast ingot improves shrinkage compensation of semi-solidified molten steel in intermediate and late solidification stages and reduces porosity of an internal structure of the cast ingot. Excitation force applied to the surface of an ingot shell at a solidified intermediate section of a continuously cast ingot breaks up dendritic crystal head growth at a solidification front edge during a cooling process in an even manner and promotes growth of equiaxed crystals.
A method for controlling the structure of a solidified cast ingot in a continuous casting process comprises: arranging a high-intensity cooling region (210) and a heating and slow-cooling region (230) in a space between a water drain port of a crystallizer and a solidification end point; performing high-intensity cooling on a continuously cast ingot (100) in the high-intensity cooling region; and then performing heating and slow-cooling on the continuously cast ingot (100) in the heating and slow-cooling region, wherein a cooling intensity of the heating and slow-cooling is less than a cooling intensity of air-based cooling. A device for employing heating and slow-cooling to control the structure of a solidified cast ingot is further disclosed, comprising a high-intensity cooling region and a heating and slow-cooling region arranged in a lengthwise direction of a continuously cast ingot at a lower portion of a continuous casting crystallizer, wherein the high-intensity cooling region is used to spray water to a surface of the cast ingot so as to perform cooling, and the heating and slow-cooling region is used to heat the surface of the cast ingot. In the method and device, a continuously cast ingot is firstly cooled in the high-intensity cooling region, and then undergoes heating and slow-cooling in the heating and slow-cooling region, thereby reducing spacing and gaps among columnar crystals, increasing efficiency of space-filling of near-surface columnar crystals on a cast ingot, and improving quality of the cast ingot.
06 - Common metals and ores; objects made of metal
12 - Land, air and water vehicles; parts of land vehicles
Goods & Services
Non-machined or semi-machined ordinary metals (terms too
vague in the opinion of the International Bureau - Rule 13
(2) (b) of the Common Regulations); metals in powder form;
metal laths; alloy steel; casting steel; big billet
(metallurgy); ordinary metal alloys, iron sand, steel sand
(terms too vague in the opinion of the International Bureau
- Rule 13 (2) (b) of the Common Regulations); angle iron;
metal tube; metal construction material; tyre steel strips
(terms too vague in the opinion of the International Bureau
- Rule 13 (2) (b) of the Common Regulations); hardware;
metal flange trays; containers; metal vessels (terms too
vague in the opinion of the International Bureau - Rule 13
(2) (b) of the Common Regulations); metal welding rods;
compressed gas or liquid air bottles (metal vessels); steel
wires; steel plates. Train wheel; train wheel hub; car chassis; rolling stock
axle; wheel; wheel hub; land vehicle speed-down gear; land
vehicle link pole (non-engine components).
06 - Common metals and ores; objects made of metal
12 - Land, air and water vehicles; parts of land vehicles
Goods & Services
Non-machined or semi-machined ordinary metals (terms too
vague in the opinion of the International Bureau - Rule 13
(2) (b) of the Common Regulations); metals in powder form;
metal laths; alloy steel; casting steel; big billet
(metallurgy); ordinary metal alloys, iron sand, steel sand
(terms too vague in the opinion of the International Bureau
- Rule 13 (2) (b) of the Common Regulations); angle iron;
metal tube; metal construction material; tyre steel strips
(terms too vague in the opinion of the International Bureau
- Rule 13 (2) (b) of the Common Regulations); hardware;
metal flange trays; containers; metal vessels (terms too
vague in the opinion of the International Bureau - Rule 13
(2) (b) of the Common Regulations); metal welding rods;
compressed gas or liquid air bottles (metal vessels); steel
wires; steel plates. Train wheel; train wheel hub; car chassis; rolling stock
axle; wheel; wheel hub; land vehicle speed-down gear; land
vehicle link pole (non-engine components).
06 - Common metals and ores; objects made of metal
12 - Land, air and water vehicles; parts of land vehicles
Goods & Services
Non-machined or semi-machined ordinary metals; powder
metallurgy; big billet (metallurgy); iron sand, steel sand;
tyre steel strips; hardware; metal flange trays; containers;
metal vessels; metal lathes; steel alloys; cast steel;
common metal alloys; angle irons; metal tubes; metal
construction materials; metal welding rods; bottles for
compressed gas or liquid air (metal vessels); steel wire;
steel plates. Land vehicle speed-down gear; land vehicle link poles
(non-engine components); train wheels; train wheel hubs; car
chassis; axles for rolling stock; wheels; wheel hubs.
23.
SYNCHRONOUS CONTROL METHOD BASED ON SYNCHRONOUS CONTROL SYSTEM FOR LIFTING HYDRAULIC CYLINDERS OF TUNDISH IN CONTINUOUS CASTING
A synchronous control method based on a synchronous control system for lifting hydraulic cylinders of a tundish in continuous casting. In the method, a position deviation that is beyond a set range and that is located between a driving hydraulic cylinder and a driven hydraulic cylinder is corrected by means of a driving and driven hydraulic cylinder synchronous position deviation speed correction unit; if the position deviation between the driving hydraulic cylinder and the driven hydraulic cylinder is beyond a set maximum allowable position deviation, the driving hydraulic cylinder at the higher speed or the driven hydraulic cylinder at the higher speed is controlled to stop moving by means of a driving and driven hydraulic cylinder synchronous position deviation overrun control unit and a driven hydraulic cylinder synchronous position deviation overrun control unit till the position deviation between the driving hydraulic cylinder and the driven hydraulic cylinder is smaller than the set maximum allowable position deviation again; and by means of a driving and driven hydraulic cylinder automatic position holding and control unit, the position deviation of the driving hydraulic cylinder and the driven hydraulic cylinder in absence of manual instructions is prevented. Accordingly, by means of the synchronous control method, synchronous movement of the driving hydraulic cylinder and the driven hydraulic cylinder can be implemented in a case in which the hydraulic cylinders leak, the manufacturing precisions of hydraulic elements are different and loads are nonuniform.
A high toughness bainitic steel wheel for rail transit, and a manufacturing method therefor. The wheel includes the following elements by weight percentage: carbon (C): 0.10-0.40%, silicon (Si): 1.00-2.00%, manganese (Mn): 1.00-2.50%, nickel (Ni): 0.20-1.00%, rare earth (RE): 0.001-0.040%, less than or equal to 0.020% of phosphorus (P), and less than or equal to 0.020% of sulphur (S), the remainder being iron and unavoidable residual elements, 1.50% ≤ Si+Ni ≤ 2.50%, 2.00% ≤ Si+Mn ≤ 4.00%. Via steel chemical composition design and manufacturing processes, the wheel rim has a carbide-free bainitic structure, the spokes and hub have a mainly granular bainitic and saturated ferritic microstructure, and the wheel has comprehensive mechanical properties such as high yield strength, toughness and low-temperature toughness, and good service usage properties. In addition, costs are reduced, and the service life and comprehensive benefits of the wheel are improved.
A low cost lean production bainitic steel wheel for rail transit, and a manufacturing method therefor. The wheel contains the following elements by weight percentage: carbon (C): 0.15-0.45%, silicon (Si): 1.00-2.50%, manganese (Mn): 1.20-3.00%, rare earth (RE): 0.001-0.04%, less than or equal to 0.020% of phosphorus (P), and less than or equal to 0.02% of sulphur (S), the remainder being iron and unavoidable residual elements, 3.00% ≤ Si+Mn ≤ 5.00%. Via alloy design and manufacturing processes, especially a heat treatment process and technique, the wheel rim has a carbide-free bainitic structure, the spokes and hub have a granular bainitic and saturated ferritic structure with a small amount of pearlite, and the wheel has high comprehensive mechanical properties and service usage properties. In addition, alloy elements such as Mo, Ni, V, Cr and B are not specially added, significantly reducing steel costs, and implementing lean production.
A high strength, high toughness, heat-cracking resistant bainite steel wheel for rail transportation and manufacturing method thereof, comprising the following components: 0.10-0.40% of carbon, 1.00-2.00% of silicon, 1.00-2.50% of manganese, 0.20-1.00% of copper, 0.0001-0.035% of boron, 0.10-1.00% of nickel, ≤ 0.020% of phosphorus, ≤ 0.020% of sulfur, and a remainder of iron and other unavoidable residual elements, wherein 1.50% ≤ Si + Ni ≤ 3.00% and 1.50% ≤ Mn + Ni + Cu ≤ 3.00%. A heat treatment technique comprises austenization heating, water quenching, and tempering treatment under 400°C.
C22C 38/02 - Ferrous alloys, e.g. steel alloys containing silicon
C22C 38/04 - Ferrous alloys, e.g. steel alloys containing manganese
C22C 38/08 - Ferrous alloys, e.g. steel alloys containing nickel
C22C 38/16 - Ferrous alloys, e.g. steel alloys containing copper
C22C 38/32 - Ferrous alloys, e.g. steel alloys containing chromium with boron
C21D 1/18 - HardeningQuenching with or without subsequent tempering
C21D 9/34 - Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor for tyresHeat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articlesFurnaces therefor for rims
27.
Straight barrel type vacuum refining device and method for use the same
Provided is a straight barrel type vacuum refining device comprising a vacuum chamber and a snorkel; during the vacuum refining the snorkel is inserted into the molten steel of the steel ladle, it is characterized in that, disposing a circulating tube being on the circumference of said snorkel, and blowing argon gas into the snorkel through the nozzles on an inner wall of a circulating tube; said circulating tubes are disposed in layers, the nozzles on the circulating tubes in the same layer are individually controlled as 2-6 in one group; disposing an eccentric gas permeable brick at the bottom of said steel ladle, and blowing argon gas into the steel ladle through the eccentric gas permeable brick, driving a circulating flow molten steel between the steel ladle and the vacuum chamber by using different blowing flow rate combinations of a steel ladle bottom blowing and each individually controlled unit of the circulating tube blowing system.
A single-impregnating-tube (1) vacuum refining device, comprising a vacuum chamber (2) and an impregnating tube (1); during vacuum refining, the impregnating tube (1) is inserted into the liquid steel of a ladle (6); blowing nozzles are peripherally disposed hierarchically on the single impregnating tube (1); the nozzles at the same layer are disposed in groups and are independently controlled; and argon gas flows into the impregnating tube (1) through the blowing nozzles on the inner wall of the single impregnating tube (1). Increase in the air throughput via the nozzles on the impregnating tube (1) in the vacuum refining process enables the liquid steel to form a circulation rising along the periphery of the vacuum chamber (2) and descending in the center of the vacuum chamber (2), thus realizing deep decarbonization and deep desulfurization under vacuum.
A straight barrel type vacuum refining device comprises a vacuum chamber (5) and an immersion tube (7). The immersion tube (7) is inserted into molten steel in a steel ladle (9) during vacuum refining. A circulating tube (8) is provided around the immersion tube (7), and argon is blown into the immersion tube (7) through a nozzle on an inner wall of the circulating tube (8); the circulating tubes (8) are provided in layers, and 2 to 6 nozzles are provided as a group to be independently controlled on the same layer of the circulating tubes (8); an eccentric breathable brick (10) is provided at the bottom of the steel ladle, argon is blown into the steel ladle through the eccentric breathable brick (10), and air blowing at the bottom of the steel ladle and a combination of different blowing flows of independently controlled units of blowing systems of the circulating tubes (8) are employed to drive the molten steel to circularly flow between the steel ladle and the vacuum chamber (5). A method for using the straight barrel type vacuum refining device is as follows: a composite blowing mode of the eccentric breathable brick (10) at the bottom of the steel ladle and the circulating tube (8) of the immersion tube (7) is employed in the vacuum refining process, the bottom blowing and the blowing of the circulating tube (8) at the same side as the bottom blowing during decarburization are strong blowing, and the blowing of the circulating tube (8) at the other side is weak blowing; and the bottom blowing is strong blowing, and the blowing of all the circulating tubes (8) around the immersion tube (7) is weak blowing during desulfurization.
