CN103882327A - Pipeline-used steel plate with excellent strain ageing performance and manufacturing method thereof - Google Patents
Pipeline-used steel plate with excellent strain ageing performance and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses a pipeline-used steel plate with excellent strain ageing performance and a manufacturing method thereof. The steel plate comprises following chemical components by weight: 0.02-0.06% of C, 0.10-0.40% of Si, 1.0-2.0% of Mn, less than 0.015% of P, less than 0.005% of S, 0.15-0.35% of Ni, 0.15-0.45% of Cr, 0.02-0.49% of Nb, not more than 0.015% of Ti, not more than 0.0002% of the limiting element H, not more than 0.004% of N, and not more than 0.0015% of O, with the balance being Fe and unavoidable impurities, wherein the ratio of the Ti to the N is not less than 3.42. The soaking temperature of slabs is 1150-1250 DEG C. Rolling is controlled in two stages, namely recrystallized zone rolling and non-recrystallized zone rolling. The cooling rate is 15-40 DEG C/s. The finish cooling temperature is controlled to be not more than 500 DEG C. The slabs are stacked and slowly cooled for 15-30 h. According to a composite design of the steel plate, combination of low carbon, the Mn, the Ni and the Cr, and preferable addition of Mo and Cu according to the thickness of the steel plate are adopted, the air cooling temperature, and the water cooling temperature and the finish cooling temperature are controlled in two stages, and therefore the pipeline-used steel plate with high strength, good plasticity and low strain ageing is obtained.
Description
Technical field
The present invention relates to the production technology of a kind of high-strength high-plasticity pipeline plate of moderate thickness, particularly relate to a kind of low-carbon (LC) Composition Design that adopts, utilization is rolled the technology that rear air cooling adds water-cool control phase transformation and is obtained required tissue morphology, produces X70 and above pipeline plate of moderate thickness and the manufacture method thereof with good strain aging performance thereof.
Background technology
Oil and gas pipes, strides forward towards the direction of major diameter, large wall thickness, high-pressure delivery apart from means of delivery as a kind of economy of oil and natural gas, length safely, uninterruptedly, and this over-all properties to pipe line steel proposes more and more higher requirement.Strain aging performance is the brand-new requirement that domestic and international pipework construction proposes, and low strain aging sensitivity is most important to the security of oil and gas pipes, particularly the pipework based on stress design.
Strain aging is that soft steel stands certain viscous deformation and is heated to after certain temperature, insulation certain hour, and the intensity of generation raises, and particularly yield strength raises obviously, a kind of phenomenon that causes yield tensile ratio significantly to raise.Pipe line steel is a kind of high added value Low-carbon Microalloyed Steel Production steel, and the heating (approximately 200 DEG C, lasting 5min) in the viscous deformation of tubulation process and corrosion protection coating preparation process can be brought out strain aging.Strain aging effect can cause disadvantageous effect to tubulation control, the construction of steel pipe site welding and steel pipe military service performance etc., and along with improving constantly of pipe line steel grade of steel, strain aging effect is more and more significant on the impact of steel tube performance.When strain aging sensitivity is higher, changing is the most significantly that stress-strain(ed) curve changes discontinuous yielding into by continuous surrender, and this is unacceptable based on stress design pipework.
In order to obtain the steel plate of low strain aging effect, a lot of technical trials are done both at home and abroad.Patent CN101456034 provides " a kind of method of the X80 of production level large-deformation resistance pipe line steel plate of moderate thickness ", this patent is not investigated the strain aging performance of steel plate, and require non-recrystallization district compression ratio to be not less than 5, can not produce with the continuously cast bloom of 230mm the steel plate of the above thickness of 27.6mm, Nb content height is at least 0.05%, higher than the addition upper limit of this patent.Patent CN101545079 provides a kind of " high-strength low-yield ratio X80 hot-rolled steel sheet and the production method thereof of good-toughness ", this patent is not investigated the strain aging performance of products made thereby equally, and while requiring recrystallization zone rolling, single pass draught is not less than 15%, increase mill load and limited Application Areas, compared with this patent, do not optimize the optimization of the element such as Cu, Mo and add scheme.Patent CN102080194 provides " a kind of large-deformation-resistance pipeline steel and production method thereof with excellent aging resistance ", in this patent, need made steel plate to carry out two-phase region quenching, although reduced strain aging sensitivity, but increased manufacturing process, reduce production efficiency and improved manufacturing cost, do not met the green Iron & Steel Development trend of " energy-saving and emission-reduction ".Patent WO2011043287 provides " a kind of high-strength high-plasticity pipe line steel and manufacture method thereof ", in this patent, C content (wt%) is 0.07%-0.15%, do not conflict for 0.02%-0.06% with this patent C content (wt%), and do not investigate the strain aging performance of its steel plate.Although the patent such as patent WO2009125863, JP2005015823 provides good steel plate preparation method, and also excellent property of made steel plate, but all do not investigate the strain aging performance of steel plate, the former does not optimize the addition of precious metal Mo, the latter need to heat-treat, complex process, compared with this patent, has increased manufacture difficulty and cost.
Summary of the invention
The present invention is based on the shortcoming that prior art exists, a kind of pipeline steel and manufacture method thereof with good strain aging performance disclosed, adopt low-carbon (LC)+Mn+Ni, Cr and according to the preferably economical Composition Design of interpolation Mo, Cu of steel plate thickness, after two-stage control rolling, air cooling adds water-cool control phase change technique, coordinate suitable final cooling temperature, obtain suitable organizational composition, obtain intensity, plasticity is good, the pipeline steel that strain aging effect is low.If adopt F+B duplex structure to form, can meet the properties requirement of X70 and above large-deformation-resistance pipeline steel plate thereof completely, and strain aging effect be very low.
For realizing the present invention's object, adopt carbon component design production X70 and above rank thereof to there is the method for the pipeline steel medium plate of good strain aging performance, comprise two aspects: the one, the economical steel plate that low-carbon (LC) adds Mn, Ni and Cr becomes offshoot program, has and selects to add Mo according to steel plate thickness; The 2nd, controlled rolling+roll the process program of rear air cooling relaxation+water-cooled+stacking slow cooling, control group is configured to the low pipe line steel of production strain aging effect.
Chemical composition composition of the present invention by wt% is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P:<0.015%, S:<0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti :≤0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable micro impurity element;
When the thickness t of steel plate exceedes after 20mm, the interpolation Mo of selection, Cu:Mo:0 ~ 0.20%, Cu:0 ~ 0.40%, preferred addition manner is [Mo%]=(t-20) × 0.01+0.02, Cu-Ni adds according to the ratio of 1:1.
Pipe line steel of the present invention adopts following operational path: reheat → controlled rolling → air cooling of get the raw materials ready → converter or electrosmelting → external refining → continuous casting → slab relaxation → control cooling → steel plate stacking slow cooling → sampling to detect.
Concrete steps are:
A) continuous casting material in set component span of control is carried out to thermal treatment again, soaking temperature is controlled in the scope of 1150-1250 DEG C, soaking time (0.2 ~ 0.6) min/mm;
B) blank after coming out of the stove is carried out to high-pressure water descaling, remove the iron scale that blank produces in heat-processed;
C) blank after de-scaling is carried out to two-stage control rolling immediately, be recrystallization zone rolling and the rolling of non-recrystallization district, recrystallization zone rolling, start rolling temperature is controlled within the scope of 1100 ~ 1200 DEG C, cumulative deformation is more than or equal to 60%, be out of shape in recrystallization zone, with the increase of deflection, austenite recrystallization grain refining effect is obvious, when deflection reaches 60% left and right, grain-size thinning effect is not obvious, finishing temperature is controlled within the scope of 1000 ~ 1100 DEG C, obtain intermediate blank, intermediate blank air cooling to 950 DEG C carries out the rolling of non-recrystallization district below again, start rolling temperature control is within the scope of 850 ~ 950 DEG C, finishing temperature is controlled within the scope of 750 ~ 850 DEG C, the control of non-recrystallization district rolling compression ratio remains on 3 ~ 7 times, the rolling of non-recrystallization district, makes austenite crystal obtain flattening and elongates, for ferrite transformation provides more active position, and the structure refinement after phase transformation.
D) the advanced line space of the steel plate after finish to gauge is cold, then water-cooled: if produce acicular ferrite (AF) shaped steel plate, water-cooled starts temperature more than Ar3 0 ~ 35 DEG C; If produce ferrite-bainite (F+B) shaped steel plate, water-cooled starts temperature below Ar3 10 ~ 60 DEG C, makes steel plate entering the ferritic phase that generates 20% ~ 80% before water cooling.Intermediate blank air cooling is treated thermophase, and niobium titanium carbonitride Second Phase Precipitation is obvious, and austenite grain boundary has obtained effectively pin, and crystal grain stability is good, and obvious alligatoring can not occur.
E) in Cooling Process, speed of cooling scope control is at 15 ~ 40 DEG C/s, and final cooling temperature is controlled at 500 DEG C and following, and the steel plate after water-cooled is improved to the laggard row stacking slow cooling of template through aligning.
F) the stacking slow cooling time is adjusted according to envrionment temperature, steel plate thickness: thickness of slab is at 20mm and following, not stacking; Thickness of slab exceedes after 20mm, envrionment temperature more than 15 DEG C, stacking 4-12 hour; Envrionment temperature below 15 DEG C, stacking 15-30 hour.Adopt air cooling relaxation+water-cooled phase transformation control, rolling rear relaxation makes steel plate obtain suitable tissue, rationally after stacking slow cooling, make steel plate there is high strength, high toughness plasticity and low strain aging effect, compared with normally used low-carbon bainite steel, Hi-Stren steel, under identical intensity rank condition, there is low yield tensile ratio, higher homogeneous deformation elongation and significantly reduced strain aging.
The thickness of described continuous casting material is preferably 230mm.
The yield strength Rt0.5 of the As rolled steel plate that the present invention finally obtains is 485 ~ 620MPa, tensile strength Rm is 605 ~ 755MPa, AF shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.82, homogeneous deformation elongation uEL >=9%, F+B shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.80, homogeneous deformation elongation uEL >=10%.
As rolled steel plate is through 200 DEG C of oil bath timeliness after 10 ~ 15 minutes, the yield strength Rt0.5 of steel plate is 495 ~ 620MPa, tensile strength Rm is 610 ~ 755MPa, AF shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.84, homogeneous deformation elongation uEL >=6%, F+B shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.82, homogeneous deformation elongation uEL >=9%.
The present invention compared with prior art, due to employing low-carbon (LC)+Mn+Ni, Cr and according to the economical Composition Design of preferred interpolation Mo, the Cu of steel plate thickness, after two-stage control rolling, air cooling adds water-cool control phase change technique, coordinate suitable final cooling temperature, obtain suitable organizational composition, obtain intensity, plasticity is good, the pipeline steel that strain aging effect is low.
Embodiment
Below by embodiment, the present invention is further described:
Moiety wt% of the present invention is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P:<0.015%, S:<0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti :≤0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable micro impurity element;
When the thickness t of steel plate exceedes after 20mm, the interpolation Mo of selection, Cu:Mo:0 ~ 0.20%, Cu:0 ~ 0.40%, preferred addition manner is [Mo%]=(t-20) × 0.01+0.02, Cu-Ni adds according to the ratio of 1:1.
Below by the preferred embodiments of the present invention, composition of the present invention, technique and implementation result are done to illustrate.
The operational path that the present invention adopts is as follows: reheat → controlled rolling → air cooling of get the raw materials ready → converter or electrosmelting → external refining → casting → slab relaxation → control cooling → stacking slow cooling → sampling to detect.
Feature of the present invention is as follows: (1) adopts low-carbon (LC) to add Mn, Ni and Cr, has the economical Composition Design of selecting to add Mo, Cu according to steel plate thickness, effectively reduces production costs.
(2) method, i.e. recrystallization zone rolling and the rolling of non-recrystallization district of the rolling of employing two-stage control.In recrystallization zone distortion, start rolling temperature is controlled within the scope of 1100 ~ 1200 DEG C, and finishing temperature is 1000 ~ 1100 DEG C of left and right, and deflection is not less than 60%, effectively refinement austenite crystal.
(3) intermediate blank air cooling is treated thermophase, and temperature is reduced to 850 ~ 950 DEG C.Niobium titanium carbonitride Second Phase Precipitation is obvious, and austenite grain boundary has obtained effectively pin, and crystal grain stability is good, and obvious grain coarsening phenomenon can not occur.
(4) non-recrystallization district rolling, start rolling temperature is controlled within the scope of 850 ~ 950 DEG C, and compression ratio remains on 3-7 doubly, and finishing temperature is controlled within the scope of 750 ~ 850 DEG C, austenite crystal is flattened and elongate, and the tissue after phase transformation obtains effective refinement.
(5) steel plate after finish to gauge carries out air cooling relaxation, and steel plate is entering the difference according to required uniform elongation before water cooling, and water-cooled starts temperature and is reduced near transformation temperature Ar3, and object is to control the organizational composition of steel plate to obtain required performance.
(6) steel plate after relaxation is carried out to water-cooled, speed of cooling scope control is at 15 ~ 40 DEG C/s, and final cooling temperature is controlled at 500 DEG C and following.
(7) by the steel plate stacking slow cooling after water-cooled to room temperature, stacking slow cooling can effectively promote separating out of niobium titanium carbonitride second-phase, reduces the C, the N atom number that exist in steel matrix, reduces plate strain ageing behavior.
Be below embodiments of the invention 1-13 and comparative example 14-16 chemical composition, processing parameter and results of property as table 1-3 as shown in, comparative example is respectively from patent CN101456034, CN102080194 and WO2009125863.
1. chemical composition
The chemical composition (wt%) of embodiment 1-12 and comparative example 13-16 is as table 1.
Table 1 chemical composition (wt%)
| C | Si | Mn | Ni | Cr | Nb | Ti | Cu | Mo | N | P | S | Thickness, mm | |
| 1 | 0.02 | 0.25 | 1.50 | 0.25 | 0.15 | 0.04 | 0.01 | 0 | 0 | 0.004 | 0.01 | 0.003 | 17.5 |
| 2 | 0.04 | 0.25 | 1.50 | 0.25 | 0.15 | 0.04 | 0.01 | 0 | 0 | 0.004 | 0.01 | 0.003 | 17.5 |
| 3 | 0.06 | 0.25 | 1.50 | 0.25 | 0.15 | 0.04 | 0.01 | 0 | 0 | 0.004 | 0.01 | 0.003 | 18.4 |
| 4 | 0.04 | 0.10 | 1.00 | 0.15 | 0.15 | 0.02 | 0.01 | 0.40 | 0.03 | 0.004 | 0.01 | 0.003 | 21 |
| 5 | 0.04 | 0.25 | 1.50 | 0.25 | 0.30 | 0.04 | 0.01 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 22 |
| 6 | 0.04 | 0.40 | 2.00 | 0.35 | 0.45 | 0.045 | 0.01 | 0 | 0.03 | 0.004 | 0.01 | 0.003 | 18.4 |
| 7 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 21 |
| 8 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 23.7 |
| 9 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0.12 | 0.004 | 0.01 | 0.003 | 28.2 |
| 10 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0 | 0.22 | 0.004 | 0.01 | 0.003 | 30 |
| 11 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0 | 0.12 | 0.004 | 0.01 | 0.003 | 40 |
| 12 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0.22 | 0.004 | 0.01 | 0.003 | 30 |
| 13 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 40 |
| 14 | 0.037 | 0.2 | 1.5 | 0.22 | 0.22 | 0.06 | 0.012 | 0 | 0 | 0.0015 | 0.005 | 0.003 | 12 |
| 15 | 0.08 | 0.22 | 1.57 | 0.25 | 0.13 | 0.03 | 0.012 | 0.04 | 0 | * | 0.008 | 0.0007 | * |
| 16 | 0.03 | 0.25 | 1.91 | 0 | 0 | 0 | 0.011 | 0.00 | 0.1 | 0.0026 | 0.007 | 0.0018 | 20 |
Note: the concrete numerical value that relevant item is not provided in * referenced patent.
2. hot rolling technology
The processing parameter of embodiment 1-13, comparative example 14-16 is in table 2.
Table 2 processing parameter
Note: the concrete numerical value that relevant item is not provided in * referenced patent.
3. results of property
Respectively the mechanical property of steel plate before and after timeliness is detected, embodiment 1-13, comparative example 14-16 performance test results are as shown in table 3.Aging test adopts oil bath, 200 DEG C of oil temperatures, and sample is incubated 12min and detects after room temperature preliminary draft 1% in oil.
Performance test results before and after table 3 timeliness
Note: the concrete numerical value that relevant item is not provided in * referenced patent.
Claims (3)
1. one kind has the pipeline steel of good strain aging performance, it is characterized in that, chemical composition composition by wt% is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P:<0.015%, S:<0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti :≤0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable micro impurity element.
2. the pipeline steel with good strain aging performance according to claim 1, it is characterized in that, when the thickness t of steel plate exceedes after 20mm, add Mo, Cu:Mo:0 ~ 0.20%, Cu:0 ~ 0.40%, addition manner is [Mo%]=(t-20) × 0.01+0.02, and Cu-Ni adds according to the ratio of 1:1.
3. the manufacture method of the pipeline steel with good strain aging performance described in a claim 1 or 2, it is characterized in that, adopt following operational path: reheat → controlled rolling → air cooling of get the raw materials ready → converter or electrosmelting → external refining → continuous casting → slab relaxation → control cooling → steel plate stacking slow cooling → sampling to detect
Concrete steps are:
A) continuous casting material in set component span of control is carried out to thermal treatment again, soaking temperature is controlled in the scope of 1150-1250 DEG C, soaking time 0.2 ~ 0.6min/mm;
B) blank after coming out of the stove is carried out to high-pressure water descaling, remove the iron scale that blank produces in heat-processed;
C) blank after de-scaling is carried out to two-stage control rolling immediately, recrystallization zone rolling, start rolling temperature is controlled within the scope of 1100 ~ 1200 DEG C, cumulative deformation is more than or equal to 60%, be out of shape in recrystallization zone, finishing temperature is controlled within the scope of 1000 ~ 1100 DEG C, obtain intermediate blank, intermediate blank air cooling to 950 DEG C carries out the rolling of non-recrystallization district below again, start rolling temperature control is within the scope of 850 ~ 950 DEG C, finishing temperature is controlled within the scope of 750 ~ 850 DEG C, and the control of non-recrystallization district rolling compression ratio remains on 3-7 doubly;
D) the advanced line space of the steel plate after finish to gauge is cold, then water-cooled: if produce acicular ferrite (AF) shaped steel plate, water-cooled starts temperature more than Ar3 0 ~ 35 DEG C; If produce ferrite-bainite (F+B) shaped steel plate, water-cooled starts temperature below Ar3 10 ~ 60 DEG C, and to become volume fraction previous existence be 20% ~ 80% ferritic phase entering water cooling to make steel plate;
E) in Cooling Process, speed of cooling scope control is at 15 ~ 40 DEG C/s, and final cooling temperature is controlled at 500 DEG C and following, and the steel plate after water-cooled is improved to the laggard row stacking slow cooling of template through aligning;
F) the stacking slow cooling time is adjusted according to envrionment temperature, steel plate thickness: thickness of slab is at 20mm and following, not stacking; Thickness of slab exceedes after 20mm, envrionment temperature more than 15 DEG C, stacking 4-12 hour; Envrionment temperature below 15 DEG C, stacking 15-30 hour.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN104789863A (en) * | 2015-03-20 | 2015-07-22 | 宝山钢铁股份有限公司 | X80 pipeline steel with good anti-strain aging property, pipeline pipe and manufacturing method of pipeline pipe |
| CN105002437A (en) * | 2015-07-02 | 2015-10-28 | 首钢总公司 | Production method of acid-resistant submarine pipeline steel low in yield ratio |
| CN106636958A (en) * | 2015-07-16 | 2017-05-10 | 中国科学院金属研究所 | Cu-containing pipeline steel and enhanced heat treatment process thereof |
| CN106702118A (en) * | 2016-12-23 | 2017-05-24 | 首钢总公司 | Cooling process for reducing work hardening effect of titanium micro-alloying high-strength steel |
| CN107988557A (en) * | 2017-12-08 | 2018-05-04 | 江苏省沙钢钢铁研究院有限公司 | With excellent strain-aging performance plus Ti pipe line steel and preparation method |
| CN111139405A (en) * | 2020-03-10 | 2020-05-12 | 唐山中厚板材有限公司 | Production method of low-cost short-process flaw detection-guaranteed medium plate |
| CN111167866A (en) * | 2020-01-04 | 2020-05-19 | 鞍钢股份有限公司 | Hardness control method for thick X80M grade pipeline bent pipe steel plate |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104789863A (en) * | 2015-03-20 | 2015-07-22 | 宝山钢铁股份有限公司 | X80 pipeline steel with good anti-strain aging property, pipeline pipe and manufacturing method of pipeline pipe |
| CN105002437A (en) * | 2015-07-02 | 2015-10-28 | 首钢总公司 | Production method of acid-resistant submarine pipeline steel low in yield ratio |
| CN105002437B (en) * | 2015-07-02 | 2017-11-10 | 首钢总公司 | A kind of production method of low yield strength ratio acid-resisting submerged pipeline steel |
| CN106636958A (en) * | 2015-07-16 | 2017-05-10 | 中国科学院金属研究所 | Cu-containing pipeline steel and enhanced heat treatment process thereof |
| CN106636958B (en) * | 2015-07-16 | 2018-09-04 | 中国科学院金属研究所 | One kind pipe line steel containing Cu and its reinforcing heat treatment process |
| CN106702118A (en) * | 2016-12-23 | 2017-05-24 | 首钢总公司 | Cooling process for reducing work hardening effect of titanium micro-alloying high-strength steel |
| CN107988557A (en) * | 2017-12-08 | 2018-05-04 | 江苏省沙钢钢铁研究院有限公司 | With excellent strain-aging performance plus Ti pipe line steel and preparation method |
| CN111167866A (en) * | 2020-01-04 | 2020-05-19 | 鞍钢股份有限公司 | Hardness control method for thick X80M grade pipeline bent pipe steel plate |
| CN111139405A (en) * | 2020-03-10 | 2020-05-12 | 唐山中厚板材有限公司 | Production method of low-cost short-process flaw detection-guaranteed medium plate |
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