CN102766820A - Hot rolled strip steel with yield strength higher than 600MPa for mine rescue capsule and preparation method of hot rolled strip steel - Google Patents
Hot rolled strip steel with yield strength higher than 600MPa for mine rescue capsule and preparation method of hot rolled strip steel Download PDFInfo
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Abstract
A hot rolled strip steel with yield strength higher than 600MPa for a mine rescue capsule and a preparation method of the hot rolled strip steel belongs to the technical field of metallurgy materials. The hot rolled strip steel comprises, by weight percent, 0.04-0.08% of C, 0.1-0.3% of Si, 1.5-1.7% of Mn, 0.01-0.05% of Al, 0.4-0.5% of Mo, 0.4-0.6% of Cr, 0.04-0.06% of Nb, 0.02-0.05% of Ti, 0.2-0.35 of Cu, not more than 0.01% of P, not more than 0.01% of S, and the balance Fe. A metallographic structure of the hot rolled strip steel is granular bainite with the yield strength no less than 600MPa, tensile strength no less than 800MPa, and elongation percentage after fracture no less than 18% at room temperature. The yield strength is no less than 450MPa, tensile strength is no less than 650MPa, and elongation percentage after fracture is no less than 19% at a high temperature of 500 DEG C. Impact energy at 20 DEG C is larger than 47J. Cold bending property is qualified. Atmospheric corrosion resistance index I under industrial environments is no less than 4.5. Sensitivity coefficient Pcm of welding cold crack is not more than 0.26%. The preparation method includes: smelting molten steel according to the preset components, casting ingots, heating, rough rolling, finish rolling to obtain the strip steel with thickness of 4-14mm, and fast cooling to obtain the finished hot rolled strip steel. The hot rolled strip steel has fine room-temperature and high-temperature mechanical performance and fine erosion resistance.
Description
Technical field
The invention belongs to the metallurgical material technical field, particularly a kind of ys is higher than the escape capsule of mine of 600MPa with hot rolled strip and preparation method.
Background technology
Escape capsule of mine is a kind of modernized safety control equipment of urgent danger prevention when protecting down-hole miner to meet with an accidet, and the mine industry is increasing for the market requirement of life-saving capsule in recent years, and the development prospect of escape capsule of mine equipment manufacture is wide.
At present, body used ferrous materials in escape capsule of mine cabin mainly is carbon structural steel and low-alloy high-strength steels such as 45 steel, Q235, Q345 and Q460, and these YIELD STRENGTH are 200 ~ 500MPa, and indexs such as toughness and bending meet the demands basically.But because the industrial environment of down-hole is complicated, the high temperature gas flow, methane and the H that for example produce during gas explosion
2Corrosive gasess such as S, the request for utilization that the hot strength of existing life-saving capsule cabin body material and corrosion resistance nature are difficult to satisfy life-saving capsule.
For this reason, develop the good special-purpose hot rolled strip of escape capsule of mine of over-all properties such as shock-resistant, high temperature resistant, corrosion-resistant that a kind of ys is higher than 600MPa and become pendulum extremely urgent task in face of scientific and technical personnel.
Summary of the invention
To the technical problem of existing escape capsule of mine with the steel existence; The present invention provides escape capsule of mine that a kind of ys is higher than 600MPa with hot rolled strip and preparation method; Purpose is to satisfy the request for utilization of escape capsule of mine with steel through suitable alloying element design and preparation method.
The escape capsule of mine that ys of the present invention is higher than 600MPa uses the hot rolled strip chemical ingredients to be C by weight percentage: 0.04 ~ 0.08 %, Si: 0.1 ~ 0.3 %, Mn:1.5 ~ 1.7 %; Al: 0.01 ~ 0.05 %, Mo:0.4 ~ 0.5 %, Cr: 0.4 ~ 0.6 %; Nb:0.04 ~ 0.06 %, Ti: 0.02 ~ 0.05 %, Cu:0.2 ~ 0.35 %; P≤0.01 %, S≤0.01 %, surplus is Fe.
Its metallographic structure is a granular bainite, room temperature ys>=600 MPa, tensile strength>=800 MPa; Elongation after fracture>=18 %, 500 ℃ of drawing by high temperature ys>=450MPa, tensile strength>=650 MPa; Elongation after fracture>=19 %, 20 ℃ of ballistic work＞47 J (impact specimen is of a size of 55 mm * 10 mm * 5 mm), cold-bending property is qualified; Atmospheric corrosion resistance sex index I>=4.5 under the industrial environment, welding cold cracking sensitivity coefficient P
Cm≤0.26 %.
The escape capsule of mine that ys of the present invention is higher than 600MPa carries out with the preparation method of hot rolled strip according to the following steps:
(1) by the chemical ingredients of setting: weight percent C: 0.04 ~ 0.08 %, Si: 0.1 ~ 0.3 %, Mn:1.5 ~ 1.7 %, Al: 0.01 ~ 0.05 %; Mo:0.4 ~ 0.5 %, Cr: 0.4 ~ 0.6 %, Nb:0.04 ~ 0.06 %; Ti: 0.02 ~ 0.05 %, Cu:0.2 ~ 0.35 %, P≤0.01 %; S≤0.01 %, surplus is the Fe smelting molten steel and casts strand that slab thickness is 150 ~ 250 mm;
(2) strand is heated to 1200 ~ 1250 ℃, is incubated 1 h, roughing 3 ~ 5 passages, the roughing start rolling temperature is 1120 ~ 1170 ℃, and finishing temperature is 980 ~ 1070 ℃, and obtaining thickness is the intermediate blank of 30 ~ 50 mm;
(3) intermediate blank is carried out finish rolling 5 ~ 7 passages, the finish rolling start rolling temperature is 950 ~ 1030 ℃, and finishing temperature is 780 ~ 860 ℃, and the finish rolling draught per pass is controlled at 15 ~ 40 %, and obtaining thickness is the band steel of 4 ~ 14 mm;
(4) the band steel after the finish rolling is cooled to 450 ~ 700 ℃ with the speed of 10 ~ 40 ℃/s, batches to obtain the thick hot rolled strip product of 4 ~ 14 mm.
What time following the design of interalloy element of the present invention considered:
C is one of solution strengthening element the most effectively in the steel, but along with the increase of C content can reduce its formability and weldableness, and low C content helps guaranteeing that steel have good moulding and toughness, therefore, the content of C is controlled in the low scope;
Mn is common reductor and sweetening agent; Can solution strengthening and phase transformation strengthening effect; Reduce
transformation temperature; Help refinement ferrite crystal grain in the course of hot rolling; The Mn element can also improve the impelling strength of steel simultaneously, reduces ductile-brittle transition temperature.But the too high levels of Mn forms segregation line easily, causes the tissue of steel and hardness inhomogeneous, and reduces the spot welding ability, so the content of Mn is controlled at about 1.6 %;
Si is a reductor commonly used in the steel, and solid solution can improve ferritic intensity effectively, but ferritic ductility is had disadvantageous effect, but the too high levels of Si is harmful to the plate surface quality in ferritic, reduces the plasticity and toughness of material.Therefore, the content of Si is controlled at about 0.2 %;
Al is that the nitrogen agent is decided in deoxidation commonly used in the steel, belongs to ferrite former, and the AlN that can form small and dispersed is as the forming core particle; Crystal grain thinning, but the too high levels of Al forms alumina inclusion easily, diminishes plasticity and toughness and welding property; Therefore, the content of Al is controlled at about 0.03 %;
Mo can significantly increase the hardening capacity of material; In high-strength steel, add Mo, hinder separating out and growing up of proeutectoid ferrite strongly, the C curve of perlite and bainite transformation is obviously separated; Make and more be prone to take place bainite transformation under the identical cooling conditions; To obtain good performance, therefore, the content of Mo is controlled at about 0.45 %;
Cr can improve the hardening capacity of steel, can improve erosion resistance and anti-hydrogen induced cracking ability simultaneously, and can improve the abrasion resistance properties of steel.The Cr element can also reduce the velocity of diffusion of C simultaneously, suppresses ferritic and perlitic transformation, and bainite transformation is moved to cold zone, reduces the bainitic transformation point, and therefore, the content of Cr is controlled at about 0.5 %;
Nb is a best element in the controlled rolling, can effectively postpone austenite recrystallization, improves austenite recrystallization temperature, thereby stops austenite crystal to grow up crystal grain thinning.Through adjustment rolling and the process for cooling parameter, Nb form deposition with carbonitride in ferritic of part solid solution attitude is separated out, ferritic is played the effect of precipitation strength.Especially under the situation that Mo exists, Nb separates out small and dispersed more, and the precipitation strength effect is also more obvious.The interaction of elements such as trace Nb and Cu, B reduces transformation temperature greatly, and bainitic transformation can be changed under lower temperature, obtains tiny lath of bainite after the phase transformation, and therefore, the content of Nb is controlled at about 0.05 %;
Ti adds trace Ti in HSLA, can improve the intensity of steel, improves the cold forming capability and the welding property of steel; Mainly utilize Ti and C, the good affinity of N; The TiN that forms, thus in the slab heating and the operation of rolling, pass through to suppress the austenite crystal that AUSTENITE GRAIN COARSENING obtains refinement, in addition; The TiN particle can suppress the grain coarsening of welded heat affecting zone, thereby improves the low-temperature flexibility of welded heat affecting zone.TiC can separate out in lower temperature, thereby produces the precipitation strength effect, but excessive Ti can damage the toughness of steel, and therefore, the content of Ti is controlled at about 0.035 %;
Cu can effectively improve the atmospheric corrosion resistance of steel, from but requisite interpolation element the weathering steel.Secondly, Cu can form tiny ε-Cu at 400 ~ 650 ℃ and separate out, and effectively improves intensity with the form of precipitation strength; Cu can also improve the welding property and the processability of steel; But excessive Cu can increase the hot cracking tendency of steel, and therefore, the content of Cu is controlled at about 0.28 %;
S and P S element are the major impurity elements that causes steel hot-short, and be prone to produce segregation and cause banded structure, and sulfide inclusion diminishes the plasticity and toughness of material, and the P element causes the cold short of steel, promptly reduces the low-temperature flexibility of material, and are easy to generate segregation.Therefore, the content of S and P should be respectively less than 0.01 %;
Adopt the foundation of controlled rolling and technology for controlled cooling: through the austenite recrystallization controlled rolling of high-temperature zone, abundant refine austenite crystal grain; The finish rolling finishing temperature is controlled at 780 ~ 860 ℃, makes the bigger accumulation strain of generation in the operation of rolling; Cool off fast the back and proper temperature batches through rolling, and obtains the granular bainite tissue.
Many particulate state islands of being made up of residual austenite or martensite are distributing in the granular bainite tissue; Matrix is played second effect of reinforcement mutually, improve work hardening capacity, reduce yield tensile ratio; Make material when improving intensity, have good moulding and toughness.Hot rolled strip metallographic structure of the present invention is a granular bainite, room temperature ys>=600 MPa, tensile strength>=800 MPa; Elongation after fracture>=18 %, 500 ℃ of drawing by high temperature ys>=450MPa, tensile strength>=650 MPa; Elongation after fracture>=19 %, 20 ℃ of ballistic work＞47 J (impact specimen is of a size of 55 mm * 10 mm * 5 mm), cold-bending property is qualified; Atmospheric corrosion resistance sex index I>=4.5 under the industrial environment, welding cold cracking sensitivity coefficient P
Cm≤0.26 %.Compare with existing general carbon steel, satisfied the industrial user demand of escape capsule of mine more with hot rolled strip.
Description of drawings
Fig. 1 is the metallographic structure figure of the hot rolled strip of the embodiment of the invention 1;
Fig. 2 is the metallographic structure figure of the hot rolled strip of the embodiment of the invention 2;
Fig. 3 is the metallographic structure figure of the hot rolled strip of the embodiment of the invention 3.
Embodiment
It is Leica DMIRM type opticmicroscope that the metallographic structure of the hot rolled strip of the embodiment of the invention is observed what adopt;
Room temperature tensile, 500 ℃ of drawing by high temperature, 180 ° of pliability tests (D=3a) all are on CMT5105-SANS microcomputer control electronics universal testing machine, to carry out;
Wherein the room temperature tensile sample is processed square-section standard tensile sample by GB/T228-2002; 500 ℃ of drawing by high temperature samples are processed square-section standard tensile sample by GB/T4338-1995; 20 ℃ of impact test equipments are Instron 9250HV drop hammer impact testing machine, and impact specimen is of a size of 55 mm * 10 mm * 5 mm.
Embodiment 1
(1) by the chemical ingredients of setting: weight percent C:0.05 %, Si: 0.2 %, Mn:1.5 %, Al: 0.01%; Mo:0.4 %, Cr:0.5 %, Nb: 0.04 %; Ti: 0.05 %, Cu: 0.2 %, P≤0.01 %; S≤0.01 %, surplus is Fe, smelting molten steel and cast the strand of 180 mm * 1300 mm * 10020 mm in 200 tons of converters;
(2) strand is heated to 1200 ℃, is incubated 1 h, rolling roughing 3 passages on 2050 mm hot continuous mills, the roughing start rolling temperature is 1120 ℃, and finishing temperature is 980 ℃, and obtaining thickness is the intermediate blank of 30mm;
(3) intermediate blank is carried out finish rolling 6 passages, the finish rolling start rolling temperature is 950 ℃, and finishing temperature is 780 ℃, and the finish rolling draught per pass is controlled at 15 ~ 40 %, and obtaining thickness is the band steel of 4 mm, adopts water-cooled between finishing stand;
(4) the band steel after the finish rolling is cooled to 450 ℃ with the speed of 40 ℃/s, batches, and the hot rolled strip product thickness that finally obtains is 4 mm.
Its metallographic structure is as shown in Figure 1, all is the granular bainite tissue, and lath of bainite interface and original austenite crystal prevention become unintelligible, the island small and dispersed that distributes on the ferrite matrix.
The mechanical property detected result is: ys 616 MPa, tensile strength 812 MPa, elongation after fracture 18.7 %; 500 ℃ of drawing by high temperature ys 461 MPa, tensile strength 667 MPa, elongation after fracture 20.2 %; 20 ℃ of ballistic work 52 J (impact specimen is of a size of 55 mm * 10 mm * 5 mm), the clod wash test passes; Atmospheric corrosion resistance sex index I=4.9 under the industrial environment, welding cold cracking sensitivity coefficient P
Cm=0.19 %.
Embodiment 2
(1) by the chemical ingredients of setting: weight percent C: 0.06 %, Si:0.3 %, Mn:1.6 %, Al:0.04 %; Mo: 0.45 %, Cr: 0.6 %, Nb: 0.05 %; Ti:0.02 %, Cu: 0.25 %, P≤0.01 %; S≤0.01 %, surplus is Fe, smelting molten steel and cast the strand of 200 mm * 1300 mm * 10020 mm in 200 tons of converters;
(2) strand is heated to 1230 ℃, is incubated 1 h, rolling roughing 4 passages on 2050 mm hot continuous mills, the roughing start rolling temperature is 1150 ℃, and finishing temperature is 1020 ℃, and obtaining thickness is the intermediate blank of 41 mm;
(3) intermediate blank is carried out finish rolling 7 passages, the finish rolling start rolling temperature is 1000 ℃, and finishing temperature is 820 ℃, and the finish rolling draught per pass is controlled at 15 ~ 40 %, and obtaining thickness is the band steel of 8 mm, adopts water-cooled between finishing stand;
(4) the band steel after the finish rolling is cooled to 610 ℃ with the speed of 28 ℃/s, batches, and the hot rolled strip product thickness that finally obtains is 8 mm.
Its metallographic structure is as shown in Figure 2, all is the granular bainite tissue, and lath of bainite interface and original austenite crystal prevention become unintelligible, the island small and dispersed that distributes on the ferrite matrix.
The mechanical property detected result is: ys 612 MPa, tensile strength 809 MPa, elongation after fracture 18.9 %; 500 ℃ of drawing by high temperature ys 459 MPa, tensile strength 661 MPa, elongation after fracture 19.8 %; 20 ℃ of ballistic work 51 J (impact specimen is of a size of 55 mm * 10 mm * 5 mm), the clod wash test passes; Atmospheric corrosion resistance sex index I=5.7 under the industrial environment, welding cold cracking sensitivity coefficient P
Cm=0.22 %.
Embodiment 3
(1) by the chemical ingredients of setting: weight percent C: 0.08 %, Si:0.1 %, Mn:1.7 %, Al:0.05 %; Mo: 0.5 %, Cr:0.4 %, Nb:0.06 %; Ti: 0.04 %, Cu: 0.35 %, P≤0.01 %; S≤0.01 %, surplus is Fe, smelting molten steel and cast the strand of 250 mm * 1300 mm * 10020 mm in 200 tons of converters;
(2) strand is heated to 1250 ℃, is incubated 1 h, rolling roughing 5 passages on 2050 mm hot continuous mills, the roughing start rolling temperature is 1170 ℃, and finishing temperature is 1070 ℃, and obtaining thickness is the intermediate blank of 50 mm;
(3) intermediate blank is carried out finish rolling 5 passages, the finish rolling start rolling temperature is 1030 ℃, and finishing temperature is 860 ℃, and the finish rolling draught per pass is controlled at 15 ~ 40 %, and obtaining thickness is the band steel of 14 mm, adopts water-cooled between finishing stand;
(4) the band steel after the finish rolling is cooled to 700 ℃ with the speed of 10 ℃/s, batches, and the hot rolled strip product thickness that finally obtains is 14 mm.
Its metallographic structure is as shown in Figure 3, is mainly the granular bainite tissue, is mingled with a small amount of quasi-polygonal ferrite, and lath of bainite interface and original austenite crystal prevention become unintelligible, the island small and dispersed that distributes on the ferrite matrix, but very uneven.
The hot rolled strip product thickness that finally obtains is 14 mm, and the mechanical property detected result is: ys 607 MPa, tensile strength 807 MPa, elongation after fracture 19.5 %; 500 ℃ of drawing by high temperature ys 457 MPa, tensile strength 658 MPa, elongation after fracture 19.6 %; 20 ℃ of ballistic work 49 J (impact specimen is of a size of 55 mm * 10 mm * 5 mm), the clod wash test passes; Atmospheric corrosion resistance sex index I=5.7 under the industrial environment, welding cold cracking sensitivity coefficient P
Cm=0.24 %.
Claims (2)
1. the ys escape capsule of mine that is higher than 600MPa is used hot rolled strip, it is characterized in that its chemical ingredients is C by weight percentage: 0.04 ~ 0.08 %, Si: 0.1 ~ 0.3 %, Mn:1.5 ~ 1.7 %; Al: 0.01 ~ 0.05 %, Mo:0.4 ~ 0.5 %, Cr: 0.4 ~ 0.6 %; Nb:0.04 ~ 0.06 %, Ti: 0.02 ~ 0.05 %, Cu:0.2 ~ 0.35 %; P≤0.01 %, S≤0.01 %, surplus is Fe;
Its metallographic structure is a granular bainite, room temperature ys>=600 MPa, tensile strength>=800 MPa; Elongation after fracture>=18 %, 500 ℃ of drawing by high temperature ys>=450MPa, tensile strength>=650 MPa; Elongation after fracture>=19 %; 20 ℃ of ballistic work＞47 J, atmospheric corrosion resistance sex index I>=4.5 under the industrial environment, welding cold cracking sensitivity coefficient P
Cm≤0.26 %.
2. a kind of ys according to claim 1 is higher than the preparation method of the escape capsule of mine of 600MPa with hot rolled strip, it is characterized in that carrying out according to following steps:
(1) by the chemical ingredients of setting: weight percent C: 0.04 ~ 0.08 %, Si: 0.1 ~ 0.3 %, Mn:1.5 ~ 1.7 %, Al: 0.01 ~ 0.05 %; Mo:0.4 ~ 0.5 %, Cr: 0.4 ~ 0.6 %, Nb:0.04 ~ 0.06 %; Ti: 0.02 ~ 0.05 %, Cu:0.2 ~ 0.35 %, P≤0.01 %; S≤0.01 %, surplus is the Fe smelting molten steel and casts strand that slab thickness is 150 ~ 250 mm;
(2) strand is heated to 1200 ~ 1250 ℃, is incubated 1 h, roughing 3 ~ 5 passages, the roughing start rolling temperature is 1120 ~ 1170 ℃, and finishing temperature is 980 ~ 1070 ℃, and obtaining thickness is the intermediate blank of 30 ~ 50 mm;
(3) intermediate blank is carried out finish rolling 5 ~ 7 passages, the finish rolling start rolling temperature is 950 ~ 1030 ℃, and finishing temperature is 780 ~ 860 ℃, and the finish rolling draught per pass is controlled at 15 ~ 40 %, and obtaining thickness is the band steel of 4 ~ 14 mm;
(4) the band steel after the finish rolling is cooled to 450 ~ 700 ℃ with the speed of 10 ~ 40 ℃/s, batches to obtain the thick hot rolled strip product of 4 ~ 14 mm.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104138900A (en) * | 2014-06-23 | 2014-11-12 | 梧州恒声电子科技有限公司 | Control method of hot-rolled steel plate |
| CN113201682A (en) * | 2021-04-15 | 2021-08-03 | 华南理工大学 | Bainite weathering steel and production method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09295067A (en) * | 1996-05-02 | 1997-11-18 | Nippon Steel Corp | Manufacture of high strength bent pipe excellent in toughness at welded metal part |
| JPH1192857A (en) * | 1997-09-16 | 1999-04-06 | Nkk Corp | Corrosion-resistant and fire-resisting steel excellent in brittle fracture resistance under high speed deformation |
| CN101736199A (en) * | 2008-11-18 | 2010-06-16 | 鞍钢股份有限公司 | Hot-rolled strip steel for high-strength cold-formed welded structure and manufacturing method thereof |
-
2012
- 2012-07-17 CN CN2012102470905A patent/CN102766820B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09295067A (en) * | 1996-05-02 | 1997-11-18 | Nippon Steel Corp | Manufacture of high strength bent pipe excellent in toughness at welded metal part |
| JPH1192857A (en) * | 1997-09-16 | 1999-04-06 | Nkk Corp | Corrosion-resistant and fire-resisting steel excellent in brittle fracture resistance under high speed deformation |
| CN101736199A (en) * | 2008-11-18 | 2010-06-16 | 鞍钢股份有限公司 | Hot-rolled strip steel for high-strength cold-formed welded structure and manufacturing method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104138900A (en) * | 2014-06-23 | 2014-11-12 | 梧州恒声电子科技有限公司 | Control method of hot-rolled steel plate |
| CN113201682A (en) * | 2021-04-15 | 2021-08-03 | 华南理工大学 | Bainite weathering steel and production method thereof |
| CN113201682B (en) * | 2021-04-15 | 2022-05-24 | 华南理工大学 | Bainite weathering steel and production method thereof |
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