CN103952643B - Low-yield ratio steel plate with yield strength of 690MPa and preparation method of steel plate - Google Patents
Low-yield ratio steel plate with yield strength of 690MPa and preparation method of steel plate Download PDFInfo
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Abstract
The invention belongs to the technical field of iron and steel and in particular relates to a low-yield ratio steel plate with yield strength of 690MPa and a preparation method of the steel plate. The low-yield ratio steel plate with the yield strength of 690MPa comprises the following chemical components in percentage by weight: 0.04-0.10% of C, 0.20-0.40% of Si, 1.40-1.90% of Mn, less than or equal to 0.020% of P, less than or equal to 0.008% of S, 0.03-0.06% of Nb 0.008-0.025% of Ti, 0.10-0.40% of Cr, 0-0.20% of Ni, 0-0.25% of Mo, 0.015-0.050% of Als, 0.0008-0.0020% of B, less than or equal to 40ppm of N, less than or equal to 20ppm of O, less than or equal to 2ppm of H and balance of Fe and inevitable impurities, wherein Als is Alsol, and welding crack sensitivity index Pcm of the steel plate is less than or equal to 0.25%. The steel plate provided by the invention has superior integrated mechanical properties, is hardly crack or break and also has good plasticity, toughness, welding property and seismic performance.
Description
Technical field
A kind of the invention belongs to iron and steel technical field, in particular it relates to yield strength 690mpa level low yield strength ratio
Steel plate and preparation method thereof.
Background technology
Economic construction and social development need substantial amounts of high-strength steel, with domestic Steel Structure Industry, engineering machinery, mine
The industries such as machinery flourish, simultaneously big for complying with the engineering machinery such as hoisting machinery, excavator boom beam, mine hydraulic support
Type, the market demand trend of high strengthening are increasingly strong to the demand of high intensity, high-quality level steel for engineering machinery.With this
Meanwhile, in order to meet high-strength steel to the requirement reducing welding crack sensibility, each big steel enterprise has put into greatly in terms of research and development
Amount manpower and materials.
In Chinese patent cn101812634a, disclose a kind of high-strength steel sheet of low-carbon low-welding crack-sensitive
Manufacture method, in terms of the composition design of steel adopt cr-cu-mo-v-nb-ti-b be combined add, the operation of rolling without controlled rolling, it
Steel plate carries out out-line quenching+tempering process again and processes afterwards, the yield strength of steel in more than 700mpa, tensile strength 800mpa with
On, yield tensile ratio is in 0.90～0.97 scope.Although this patent also provides a kind of low welding crack sensitivity steel plate of 80kg level
Production method, but be disadvantageous in that fine grain, phase transformation and the dislocation failing to make full use of the controlled rolling and controlled cooling in the operation of rolling is strong
Change mechanism, simultaneously steel plate also need to carry out out-line quenching and tempering heat treatment, cause production cost increase.
In Chinese patent cn101418418b, disclose a kind of yield strength 690mpa level low-crackle sensitive steel
Manufacture method, adopts cr-mo-v-nb-ti-b to be combined in terms of the composition design of steel and adds, the yield strength of steel 690mpa with
On, in more than 770mpa, yield tensile ratio is in 0.87～0.91 scope for tensile strength.Although this patent provides one kind without any
The method that heat treatment just can produce the low welding crack sensitivity steel plate of 80kg level, but add 0.04～0.12% valuable gold
Belong to v, cause this steel grade cost of alloy higher.
In Chinese patent cn100439545c, disclose a kind of manufacture of 800mpa grade high ductility low-yield ratio thick steel plate
Method, adds 0.30%～0.70% precious metal ni in the composition design of steel, causes cost of alloy higher, and should
Steel plate yield strength only can guarantee that more than 540mpa.
Find to after prior art analysis, in disclosed document, the yield strength of most of steel plate is not higher than
690mpa, or yield strength reaches 80kg rank, but the higher yield tensile ratio simultaneously of production cost is higher, and safety is not enough.
Content of the invention
It is an object of the invention to provide a kind of yield strength 690mpa level low yield strength ratio steel plate and further provide for this
The preparation method of low yield strength ratio steel plate, by the control to chemical composition and rolling mill practice, obtains one kind by needle-like in steel plate
Special heterogeneous structure based on ferrite, quasi-polygonal ferrite and ferrite bainite, forms the collocation of soft or hard phase, lifting steel plate should
Become hardenability value, it is achieved thereby that the production of yield strength 690mpa level low yield strength ratio steel plate is it is ensured that the safety such as steel structure earthquake-resistant
Index.
For reaching above-mentioned purpose, the yield strength 690mpa level low yield strength ratio steel plate of the present invention, its chemical composition is by weight
Percentages comprise: c:0.04%～0.10%, si:0.20%～0.40%, mn:1.40%～1.90%, p≤0.020%,
S≤0.008%, nb:0.03%～0.06%, ti:0.008%～0.025%, cr:0.10%～0.40%, ni:0%～
0.20%th, mo:0%～0.25%, als:0.015%～0.050%, b:0.0008～0.0020%, n≤40ppm, o≤
20ppm, h≤2ppm, remaining is ferrum and inevitable impurity, and wherein, als represents dissolved aluminum.The weld crack of described steel plate
Sensitivity Index pcm≤0.25%, the steel chemical composition of the present invention meets:
Pcm=c+si/30+mn/20+cu/20+ni/60+cr/20+mo/15+v/10+5b≤0.25%.
The yield strength 690mpa level low yield strength ratio steel plate of the present invention, its yield strength >=690mpa, yield tensile ratio≤0.83.
Hereinafter the chemical composition of the yield strength 690mpa level low yield strength ratio steel plate of the present invention is described in detail.
C:c is topmost solution strengthening element, can significantly improve the quenching degree of steel, is also most economical in mild steel
Intensified element, the intensity to martensite steel and hardness play conclusive effect, but the increase of carbon content makes plasticity and the impact of steel
Toughness reduces, and cold short tendentiousness and timeliness tendentiousness improve, and deteriorate welding performance.Must additionally increase in view of while carbon drop
Other valuable microalloy content guarantee hardness of steel, and this will result in cost and increases considerably, it is suitable by c to consider
Amount controls 0.04%～0.10%.
Si:si enters ferrite and plays solution strengthening effect, reduces yield tensile ratio, but si can significantly increase the ductile-brittle transiton of steel
Temperature, also can deteriorate plasticity and welding performance simultaneously, and therefore, the Sq of si controls 0.20%～0.40%.
Mn:mn can reduce critical transition temperature ar3 hence it is evident that improving the quenching degree of steel, have certain solid solution strong simultaneously
Change acts on, and plays the raising intensity of steel and the effect of hardness.Because manganese and sulfur have larger affinity, mns has in high temperature
Certain plasticity, it is to avoid steel hot-short, but too high mn can affect the welding performance of steel, and the center that also can aggravate strand is inclined
Analysis, causes product banded structure serious, and then has influence on impact flexibility.Therefore, the Sq of mn control 1.40%～
1.90%.
P:p belongs to black brittleness element, and p is significantly expanded the two-phase section between liquid phase and solid phase, in steel process of setting partially
Analyse between crystal grain, form high phosphorus brittle layer, improve the rank of banded structure, make the local organization of steel abnormal, cause mechanicalness
Can be uneven, reduce the plasticity of steel, make steel be also easy to produce brittle crack, corrosion resistance declines, and welding performance is also adversely affected,
Increase welding crack sensibility, so content in steel for the phosphorus should be reduced as far as possible.In view of production cost, by the content control of p
System is below 0.020%.
S: when s presented in fes in steel when, if s content height, be also easy to produce hot-short phenomenon.When s is with the shape of mns
When formula is present in steel, s is often distributed along rolling direction with bar form, forms serious banded structure, destroys the continuous of steel
Property, material impact also can be produced to the performance of steel different directions, reduce plasticity and the impact flexibility of steel, improve ductile-brittle transiton temperature
Degree.Therefore, the content of s is controlled below 0.008%.
Nb:nb can produce significant crystal grain refinement, precipitation strength and medium precipitation enhancement.It is solid-solution in austenite
Nb can improve quenching degree, nb (c, n) precipitated phase there is Grain refinement but reduce quenching degree, and work as nb too high levels
When, nb is easily and the element such as fe, c forms Low melting point eutectic, has the tendency of to increase welding heat affected zone fire check.Comprehensive each side
Factor, the Sq of nb controls between 0.03%～0.06%.
Ti:ti can separate out tin granule under 1200～1300 DEG C of high temperature, can as the precipitation core of nb (c, n), from
And reduce the quantity of fine niobium precipitate, and then reduce the crack sensitivity containing nb steel.Ti can be formed tiny titanium carbide,
Nitride particles, pass through to stop the roughening of austenite crystal to show thus obtaining comparatively fine austenite during heating of plate blank
Micro-assembly robot.Ti is combined with n and generates stable high diffusive compound, not only can eliminate the free nitrogen in steel, and can add in heat
Control crystallite dimension in heat affected area when work process and welding, improve the low-temperature flexibility at each position of steel construction.Excessive ti will
Form liquation tin of micron order size, do not simply fail to crystal grain thinning, steel plate toughness can be deteriorated on the contrary.Therefore, the Sq control of ti
Make 0.008%～0.025%.
Cr:cr can prevent plus the graphitization of mo steel is inclined to, and belong to stable austenite element, can be greatly enhanced the through hardening of steel
Property, improve the intensity of steel, but too high cr can reduce the welding performance of steel, considers, the Sq of cr controls 0.10%
～0.40%.
Ni:ni plays a part reinforced ferrite by forming simple substitution solid solution, can improve the intensity of steel, simultaneously
Ni is among the austenite stabilizing elements, is remarkably improved the low-temperature impact-resistant toughness of steel.But, ni plate price is relatively expensive, examines
Consider cost factor, the Sq of ni controls 0%～0.20%.
Mo:mo is present in solid solution phase and Carbide Phases in steel, belongs to stable austenite element, can be greatly enhanced
C curve can be moved to right by the quenching degree of steel strongly, to promote martensite transfor mation, can improve steel belt roof bolt fragility simultaneously, greatly carry
The low-temperature flexibility of Gao Gang, improves the resistance for delayed fracture of steel.Integrated cost factor, the Sq of mo controls 0%～
0.25%.
Al:al can refine the crystal grain of steel, improve the intensity of steel, also can improve impact flexibility simultaneously.Due to al and n have stronger
Affinity, the aging sensitivity that n element causes can also be eliminated, therefore, the content of als is set to 0.015%～0.050%.
The strong segregation of b:b is at austenite grain boundary and other crystal defect, by increasing capacitance it is possible to increase the hardenability of steel, improves quenching of steel
Permeability.The forming core adding micro b can substantially suppress ferrite on austenite grain boundary, makes ferritic transformation curve substantially move to right,
To promote martensite transfor mation, but Boron contents more than 0.002% after above-mentioned effect reach saturation, but also be likely to form various to heat
Processing characteristics and the unfavorable precipitated phase containing b of toughness, consider, Boron contents should control 0.0008%～0.0020%.
N:n too high levels can deteriorate the impact flexibility of high-strength steel, and general control is in below 40ppm.
O:o too high levels show that steel inclusion is too many, and every mechanical performance of steel all can be had adverse effect on, therefore
O content should control in below 20ppm as far as possible, to improve Cleanliness of Molten Steel.
, for the high-strength steel that yield strength is more than 690mpa, harm is larger, easily causes flaw detection and does not conform to, and affects for h:h
Low-temperature impact toughness, needs to control in below 2ppm by means such as applications of vacuum.
The present invention is directed to the steel plate of different-thickness, optimizes composition design, and Thin Specs walk low-carbon high-manganese high nb no precious metal
As the route of ni, mo, because carbon content is relatively low, mn content is greatly improved simultaneously and can be effectively improved steel plate toughness and plasticity, then coordinate
The rational of technique, on the premise of ensureing the function admirables such as yield tensile ratio, realizes low cost；Think gauge can suitably reduce nb unit
Cellulose content, adds a small amount of ni, mo element simultaneously, and its effect is: think gauge is proof strength, and carbon increases, and adds ni unit
Element can improve the toughness of steel plate, add mo element and be conducive to c curve to move to right, beneficial in the hard phase constitution of strong cool condition lower bainite
Formed, thus obtaining the relatively low yield tensile ratio performance of high-strength steel.
Present invention also offers the preparation method of above-mentioned yield strength 690mpa level low yield strength ratio steel plate, including smelting, pour
Casting, heating, rolling and cooling step, wherein:
Heating-up temperature before (a) rolling: steel billet tapping temperature controls at 1150～1220 DEG C；
(b) rolling condition: workpiece thickness is 2.0～4.0 times of finished product thickness, steel billet finish rolling start rolling temperature is 900～
1020 DEG C, finishing temperature is 860～920 DEG C；
(c) cooling condition: open cold temperature be 720～800 DEG C, final cooling temperature be 480～580 DEG C, rate of cooling be 14～
22℃/s.
Specifically, the preparation method of the yield strength 690mpa level low yield strength ratio steel plate of the present invention, comprises the following steps:
Smelt and cast: using converter or electric furnace smelting, casting adopts continuous casting or molding.
Using heavy and medium plate mill rolling:
Heating-up temperature before (a) rolling: steel billet tapping temperature controls at 1150～1220 DEG C.In order to give full play to nb, ti
Postpone the effect such as precipitation strength during austenite recrystallization, rolling and roller repairing Deng microalloy element in During Controlled Rolling,
Should ensure that microalloy element is more solidly soluted in austenite, give full play to its solid solution advantage, so billet heating temperature is at least
More than 1150 DEG C should be improved；Simultaneously take account of heating-up temperature too high, austenite crystal is too grown up, and be genetic to and roll rear steel
Plate, can have undesirable effect to steel plate impact flexibility, therefore should ensure that steel billet tapping temperature controls below 1220 DEG C as far as possible.
(b) rolling condition: workpiece thickness is 2.0～4.0 times of finished product thickness, steel billet finish rolling start rolling temperature is 900～
1020 DEG C, finishing temperature is 860～920 DEG C.Steel billet obtains middle base after roughing mill rolling, treats that temperature arrives target on roller-way
After start rolling temperature, carry out finish rolling.Finishing stands roll rear crystal grain refinement for guarantee, improve steel plate comprehensive mechanical property, need fully
Play Second Phase Particles nb (c, n) pinning dislocation, stop austenite recrystallization, improve tnr temperature (recrystallization final temperature)
, to expand controlled rolling process window, particularly with Thin Specs high strength steel plate, easily the plate shapes such as wooden dipper song, middle wave, Bian Lang and asks in effect
Topic, so finish rolling start rolling temperature should be improved as far as possible to reduce rolling drag, start rolling temperature also to be avoided is higher than that tnr is produced simultaneously
Raw mixed crystal phenomenon, therefore finish rolling start rolling temperature, not above 1020 DEG C, simultaneously for ensureing think gauge plate shape, reduces rolling load,
Therefore finish rolling start rolling temperature cannot be below 900 DEG C.
With middle base temperature drop to below tnr, austenite crystal recrystallization is suppressed, by big pressure rolling,
Austenite crystal is in flatten and elongated condition, produces a large amount of glide bands and dislocation with the increase of drafts, crystal grain, increases
Effectively grain boundary area, increases phase transformation thinning effect, improves the obdurability of steel, simultaneously takes account of thick steel plates and should ensure that roughing rank
Enough drafts of section, with uniform refinement section of steel plate tissue, consider, workpiece thickness should control in finished product thickness
2.0～4.0 times.
(c) cooling condition: open cold temperature be 720～800 DEG C, final cooling temperature be 480～580 DEG C, rate of cooling be 14～
22℃/s.During this invention Plate Production, after controlling finish to gauge in the tissue starting before acceleration cooling and morphotropism body
The Physical Metallurgy processes such as defect relaxed state, the pick-up behavior of microalloy element, realize controlling the phase transformation of steel, and final acquisition is ultra-fine
Complex tissue.With the formation of relaxation process pro-eutectoid ferrite, carbon atom is also constantly spreading to adjacent tissue, causes future
And the carbon content of austenite structure of phase transformation substantially increase, further enhancing the structure stability of non-transformed austenite and promote
C curve is made to move to right, after entering water, this region will be easier to be transformed into the hard phase constitution of low temperature of bainite etc, promotes under yield tensile ratio
Fall, simultaneously takes account of armor plate strength surplus capacity after phase transformation, therefore opens cold temperature and be suitably reduced in the range of 720～800 DEG C.
By properly increasing final cooling temperature, reduce tissue middle plate strip bayesian body burden, and formed original austenite grain is had
The acicular ferrite structure of segmentation effect, the increase of soft Phase Proportion and the variation of form are beneficial to reducing yield tensile ratio,
Simultaneously take account of final cooling temperature too high, armor plate strength surplus capacity is by deficiency, therefore final cooling temperature controls in the range of 480～580 DEG C.
With the increase of rate of cooling, promote the transformation to cryo tissue for the non-transformed austenite, improve ferrite bainite hard
Phase constitution volume fraction, thus having pulled open the hardness difference of soft and hard alternation, improving steel plate tensile strength, realizing yield tensile ratio significantly
Decline, meanwhile, the raising of cooling rate is also beneficial to the Dispersed precipitate on Ma Ao island, thus improving steel plate low-temperature flexibility, but too high cooling rate
Also the plasticity and toughness of steel plate can be deteriorated, consider, rate of cooling controls in the range of 14～22 DEG C/s.
The steel plate of the present invention has high intensity, low yield strength ratio and has low-welding crack-sensitive, beneficial to promoting the use of.
It is an advantage of the current invention that:
(1) by reasonably optimizing is carried out to composition, the precious metals such as v are replaced using the cheap alloy such as c, cr, b, in conjunction with heat
The advanced technology of mechanical controlled rolling and controlled cooling, to be realized with a low cost the production of yield strength 690mpa level high strength steel plate.
(2) steel of the present invention not only has excellent low-temperature flexibility, elongation after fracture and relatively low weld crack sensitivity
Index, but also there is relatively low yield tensile ratio it is ensured that welded steel structure possesses excellent anti-seismic performance, overall security is more
Good.
(3) steel of the present invention is produced using cooling controlling and rolling controlling process, need not carry out heat treatment after rolling, and can simplify production work
Sequence, is greatly reduced production cost, also can substantially shorten the delivery cycle, comprehensive benefit is notable simultaneously.
In sum, the comprehensive mechanical property of steel of the present invention is superior, not easy fracture and destruction, and have good mould tough
Property, welding performance and anti-seismic performance, safe and reliable, can be widely applied to coal mine hydraulic supporting, high speed double-tracking railways bridge,
Ocean platform etc. has the large-scale engineering machinery equipment of strict demand or the manufacture of steel construction to antidetonation security performance.
Brief description
Fig. 1 is the sem micro-organization chart of the made steel plate of the present invention.
Specific embodiment
Chemical composition chemical composition as shown in table 1 of yield strength 690mpa level low yield strength ratio steel plate according to the present invention is entered
Row converter smelting simultaneously pours into continuous casting billet or ingot casting, will heat, using cut deal after continuous casting billet or ingot formation in heating furnace
Mill milling, rolls rear steel plate without heat treatment.The main technologic parameters such as strand tapping temperature, finishing temperature, final cooling temperature are shown in Table
2.Corresponding steel plate stretching intensity, -40 DEG C of impact of collision work(, thickness specifications list in table 3 it is seen that the low-temperature impact of steel of the present invention
Tenacity excellent, -40 DEG C of longitudinal akv are not less than 150j.Fig. 1 shows the sem microstructure photo of embodiment 6 steel, display tissue
For acicular ferrite+quasi-polygonal ferrite+ferrite bainite.
Table 1 below illustrates the chemical composition of the steel of 1 to embodiment 8 according to embodiments of the present invention.
The chemical composition (wt.%) of table 1 embodiment of the present invention
Table 2 below shows the main technologic parameters of 1 to embodiment 8 according to embodiments of the present invention.
The main production parameter of table 2 embodiment of the present invention
Table 3 shows the Main Mechanical of 1 to embodiment 8 according to embodiments of the present invention.
The mechanical property of table 3 embodiment of the present invention
Those of ordinary skill in the art it should be appreciated that above embodiment be intended merely to illustrate the present invention,
And be not used as limitation of the invention, the change as long as in the spirit of the present invention, to embodiment described above
Change, modification all will fall in the range of claims of the present invention.
Claims (4)
1. a kind of yield strength 690mpa level low yield strength ratio steel plate is it is characterised in that the chemical composition by weight hundred of described steel plate
Divide and comprise than meter: c:0.04%～0.10%, si:0.20%～0.40%, mn:1.40%～1.90%, p≤0.020%, s
≤ 0.008%, nb:0.03%～0.06%, ti:0.008%～0.025%, cr:0.10%～0.40%, ni:0%～
0.20%th, mo:0%～0.25%, als:0.015%～0.050%, b:0.0008～0.0020%, n≤40ppm, o≤
20ppm, h≤2ppm, remaining is ferrum and inevitable impurity；Weld crack Sensitivity Index pcm≤0.25% of described steel plate；
Described low yield strength ratio steel plate tissue composition includes acicular ferrite, quasi-polygonal ferrite and ferrite bainite；Described steel plate-
40 DEG C of impact of collision work(are not less than 150j.
2. low yield strength ratio steel plate according to claim 1 it is characterised in that described low yield strength ratio steel plate yield strength >=
690mpa, yield tensile ratio≤0.83.
3. the preparation method of low yield strength ratio steel plate described in a kind of claim 1 or 2, including smelting, casting, heating, rolls and cold
But step, wherein:
Heating-up temperature before (a) rolling: steel billet tapping temperature controls at 1150～1220 DEG C；
B () rolling condition: workpiece thickness is 2.0～4.0 times of finished product thickness, steel billet finish rolling start rolling temperature is 900～1020
DEG C, finishing temperature is 865～920 DEG C；
(c) cooling condition: open cold temperature be 720～800 DEG C, final cooling temperature be 510～580 DEG C, rate of cooling be 14～22 DEG C/
s.
4. preparation method according to claim 3 need not carry out heat treatment it is characterised in that rolling rear steel plate.
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| CN104278206A (en) * | 2014-10-15 | 2015-01-14 | 山东钢铁股份有限公司 | Steel plate with thickness of smaller than 60mm and yield strength of 690MPa and preparation method of steel plate |
| CN104278216A (en) * | 2014-10-15 | 2015-01-14 | 山东钢铁股份有限公司 | Steel plate with thickness of larger than 60mm and yield strength of 690MPa and preparation method of steel plate |
| CN104492809A (en) * | 2014-12-12 | 2015-04-08 | 本钢板材股份有限公司 | High-strength steel rolling method |
| CN105441790A (en) * | 2015-11-11 | 2016-03-30 | 广东韶钢松山股份有限公司 | Steel plate with low welding crack sensitivity and manufacturing method thereof |
| CN107675097B (en) * | 2017-08-15 | 2020-05-29 | 河钢股份有限公司邯郸分公司 | High-strength steel Q690D steel plate with good side bending performance and production method thereof |
| CN108823489B (en) * | 2018-05-29 | 2020-07-03 | 唐山中厚板材有限公司 | 600 MPa-grade hydroelectric steel plate and production method thereof |
| CN109023068B (en) * | 2018-09-04 | 2020-09-01 | 鞍钢股份有限公司 | Steel plate for VC (polyvinyl chloride) nanoparticle reinforced X90 plastic pipe and manufacturing method thereof |
| CN109719146B (en) * | 2019-01-07 | 2020-11-17 | 东北大学 | Efficient descaling method for high-surface-quality medium plate product |
| CN111979478B (en) * | 2020-07-08 | 2022-08-09 | 邯郸钢铁集团有限责任公司 | Thin SAPH440 strip steel and production method thereof |
| CN112553532A (en) * | 2020-12-04 | 2021-03-26 | 山东钢铁集团日照有限公司 | High-toughness reduced ship plate marine steel and preparation method thereof |
| CN112410686B (en) * | 2020-12-04 | 2022-08-05 | 安阳钢铁股份有限公司 | Low-yield-ratio high-strength steel plate and production method thereof |
| CN114134416B (en) * | 2021-11-16 | 2022-10-25 | 山东钢铁集团日照有限公司 | Low-yield-ratio high-strength medium-thickness steel plate and short-process manufacturing method thereof |
| CN114959509B (en) * | 2022-08-02 | 2022-11-18 | 江苏省沙钢钢铁研究院有限公司 | 690 MPa-grade high-toughness steel plate and production method thereof |
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| CN101649425B (en) * | 2009-09-08 | 2011-10-05 | 武汉钢铁(集团)公司 | X120 pipeline steel with low crack sensitivity and high toughness and manufacturing method thereof |
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Inventor after: Yang Jianxun Inventor after: Liu Fei Inventor after: Chu Lin Inventor after: Zhang Xiaomin Inventor after: Sun Zhengxiao Inventor after: Wang Jianjing Inventor after: Wang Fei Inventor after: Huang Chunsheng Inventor before: Yang Jianxun Inventor before: Liu Fei Inventor before: Wang Jianjing Inventor before: Wang Fei Inventor before: Wang Jing Inventor before: Qin Gang Inventor before: Huang Chunsheng Inventor before: Wang Yanguo |
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Effective date of registration: 20220623 Address after: 271104 Shuangquan Road, Gangcheng District, Jinan City, Shandong Province Patentee after: LAIGANG GROUP YINSHAN SHAPED STEEL Co.,Ltd. Address before: 271104 No.99, Fuqian street, Gangcheng District, Laiwu City, Shandong Province Patentee before: LAIWU STEEL Group Ltd. |