CN102251086A - Molybdenum-based ferrite stainless steel and preparation method thereof - Google Patents
Molybdenum-based ferrite stainless steel and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a preparation method for molybdenum-based ferrite stainless steel. The molybdenum-based ferrite stainless steel comprises the following chemical components, by weight, 0.004-0.012%, of C, 0.008-0.020% of N, less than or equal to 0.030% of (C+N), 0.10-0.50% of Si, less than or equal to 0.50% of Mn, 17.00-22.50% of Cr, 1.70-2.50% of Mo, 0.15-0.45% of Nb, 0.20*10<-4>*(Cr)/(N) -0.25% of Ti and 0.005-0.010% of O, the balance of inevitable impurities and Fe as a balance element. The preparation method for the molybdenum-based ferrite stainless steel is characterized by: carrying out smelting, continuous steel casting or die casting, heating and controlling a temperature of a continuous casting billet or a die billet to 1000-1100 DEG C to enable the ferrite structure to be uniformized; completing hot rolling at the temperature more than 800 DEG C, followed by carrying out cooling; carrying out continuous annealing for the hot rolled coil at the temperature of 950-1050 DEG C, followed by carrying out acid cleaning; carrying out cold rolling having cumulative reduction rate more than or equal to 70%, followed by carrying out continuous annealing, wherein the annealing temperature is 950-1050 DEG C, then carrying out acid cleaning. The welding position of the prepared molybdenum-based ferrite stainless steel through the method provided by the present invention has excellent toughness, and can meet a high-toughness requirement of the welding position on the ferrite stainless steel in the water treatment system industry.
Description
Technical field
The present invention relates to ferritic stainless steel and manufacture method thereof, particularly a kind of welding zone good-toughness contain molybdenum type ferritic stainless steel and manufacture method thereof.
Background technology
Ferritic stainless steel all has a wide range of applications and vast potential for future development in industries such as automobile exhaust system, tame electrical article, building structure, water treatment systems because it has cost risk little (not containing or contain minor N i), the good characteristics of solidity to corrosion (particularly anticorrosion stress-resistant, spot corrosion, crevice corrosion).In the water treatment system industry, states such as America and Europe and Japan have begun to widely apply the super-purity ferrite stainless steel that contains the molybdenum type, and representing steel grade is SUS444.Traditional ferritic stainless steel has the shortcoming of ductile-brittle transition temperature height, poor in processability etc., adopts modern advanced stainless steel production technology, can guarantee that typical impurity element C, N, P, S etc. remain in the lower scope.In addition, also can add performance and the processibility that stabilizing elements such as Ti, Nb, Zr improve super-purity ferrite stainless steel itself according to different demands.
Usually, ferritic stainless steel is applied to the occasion of thin plate, and therefore, its situation of not adding welding material is very many.Welding process commonly used has argon tungsten-arc welding, resistance welding, Laser Welding, plasma arc welding etc., but adopts the problem of these welding processs to be, crystal grain is thick to have caused the ductility of welding zone and toughness low, and finally also causes the welding processing of thin plate poor.
The welding property introduced good stainless material is arranged in the prior art, as publication number be JP02-107744 Japanese Patent Application Publication the ferrite-group stainless steel of a kind of weldability and excellent corrosion resistance, this technology by make Si content 1.0～2.0% with interior, Mn content 0.5% to guarantee the weldability and the mechanical property of mother metal down, in addition, solidity to corrosion, the plasticity of mother metal and weld also significantly improve, this technology does not stipulate that Nb, Ti must add simultaneously, and looks necessary the Cu element that added.
Publication number be JP03-031448 Japanese Patent Application Publication a kind of ferrite-group stainless steel of tenacity excellent of weld, this technology improves the intensity of welding zone by generating martensite, thereby obtains good welding zone performance.This technology obtains certain ratio of martensite by adjusting chemical ingredients, need not Nb, Ti stabilizing element, and the scope of its C, N content is also than broad, and purpose is in order to obtain martensite.
Publication number be JP04-224657 Japanese Patent Application Publication the ferrite-group stainless steel of tenacity excellent at a kind of hot strength and welding heat affected position, by adding Co or compound interpolation Ti, Co, make the hot strength of designed steel grade obtain improvement, welding heat influence area toughness is improved.
Publication number be JP04-228539 Japanese Patent Application Publication the ferrite-group stainless steel of a kind of hot strength and weld excellent in workability, improve design steel grade hot strength by one-tenth balance-dividing and the interpolation Mo that finds out C, N, Nb, and by reducing C, N content and adding the processing characteristics that V improves the weld.
Publication number be JP05-033104 Japanese Patent Application Publication the ferritic series heat-resistance stainless steel of a kind of thermotolerance, low-temperature flexibility and welding property excellent, by compound interpolation Mo, Cu, and regulation Mn/S is more than 200, to improve the hot strength of design steel grade, it adds Ti, Nb all is in order to guarantee to design the hot strength of steel grade.
Publication number be JP05-070899 Japanese Patent Application Publication the ferrite-group stainless steel of a kind of weld excellent corrosion resistance, form the easier formation of oxide compound that makes Al by compound interpolation Ti, Al, in welding process, the oxide compound of Al can prevent the oxidational losses of Cr, and the solidity to corrosion of weld just can be improved like this.
Publication number be JP09-217151 Japanese Patent Application Publication a kind of ferrite-group stainless steel of welding property excellent, equiax crystalization, grain refining have been realized by compound interpolation Al, Mg so that design the weld tissue of steel grade, with ductility and the toughness of improving the weld.
Publication number be JP01-081940 Japanese Patent Application Publication a kind of ferrite-group stainless steel of welding portion excellent corrosion resistance, by increasing Cr, Mo, and compound interpolation Ti, Al and add the corrosion resistance nature that proper C u improves design steel grade weld.
Publication number be JP2002-121653 Japanese Patent Application Publication all excellent ferritic stainless steel and the manufacture method thereof of a kind of cold-workability, erosion resistance, machinability, weldability, add Si by trace and improve weldability, and guarantee the amount of separating out of Nb carbonitride, thereby obtain the grain refining of weld by the lower limit that adds Nb and regulation (C+N).
But the ferrite stainless steel capital of above prior art can not reach the water treatment system industry to containing the requirement of molybdenum type ferritic stainless steel welding zone high tenacity.
Summary of the invention
What the object of the present invention is to provide that a kind of welding zone has an excellent in toughness contains molybdenum type ferritic stainless steel.
To achieve these goals, ferritic stainless steel of the present invention, its chemical component weight per-cent is: C:0.004～0.012%, N:0.008～0.020%, (C+N)≤0.030%, Si:0.10～0.50%, Mn≤0.50%, Cr:17.00～22.50%, Mo:1.70～2.50%, Nb:0.15～0.45%, Ti:0.20 * 10
-4* (Cr)/(N)～0.25%, and O:0.005～0.010%, all the other are unavoidable impurities and balance element of Fe.
Preferably, Mn:0.10～0.50%.
Preferably, composition of the present invention also satisfies: value (Nb)/(Ti) is 1.5～4; (Nb+Ti)/(C+N) value is 12～22.
Another object of the present invention provides a kind of stainless manufacture method of molybdenum type ferrite that contains.
For realizing this purpose, the present invention is by control composition and processing range, and what produce that its welding zone has an excellent in toughness contains molybdenum type ferritic stainless steel.Steel of the present invention is a kind of Nb, Ti bistableization and the ferrite stainless steel that contains Mo, and its welding zone has excellent in toughness.
The molybdenum type ferritic stainless steel manufacture method that contains of the present invention comprises:
(1) with weight percent is C:0.004～0.012%, N:0.008～0.020%, (C+N)≤0.030%, Si:0.10～0.50%, Mn≤0.50%, Cr:17.00～22.50%, Mo:1.70～2.50%, Nb:0.15～0.45%, Ti:0.20 * 10
-4* (Cr)/(N)～0.25%, and O:0.005～0.010%, all the other are unavoidable impurities and balance element of Fe, preferably, and Mn:0.10～0.50%, preferably, also satisfy: value (Nb)/(Ti) is 1.5～4; (Nb+Ti)/(C+N) value is smelted by electric furnace-AOD-VOD three-step approach at 12～22 composition;
(2), the temperature of continuously cast bloom or die casting base is controlled at 1000～1100 ℃ by heating;
(3) finish hot rolling more than 800 ℃, the hot rolling postcooling preferably, is finished hot rolling at 800～860 ℃;
(4) hot rolled coil is finished continuous annealing at 950～1050 ℃, and the continuous annealing system is 0.5～1.5min/mm, and promptly every 1mm thickness annealing time is 0.5～1.5min; Carry out pickling after the annealing;
(5) cold rolling accumulation draft 〉=70% carries out continuous annealing after cold rolling, and annealing temperature is 950～1050 ℃, and the continuous annealing system is 0.5～1.5min/mm; Carry out pickling after the annealing.
Preferably, cold rolling accumulation draft is 70～85%.
What another purpose of the present invention provided a kind of above-mentioned manufacture method manufacturing contains molybdenum type ferrite stainless steel cold-rolled plate.
The composition of the ferritic stainless steel of object of the present invention limits and the reasons are as follows:
C content:, consider also to need certain content from the intensity angle though C is harmful to erosion resistance.If C content is very low, be lower than 0.004%, production cost just improves; And if content surpasses 0.010%, then when processibility, toughness descend, owing to, form the compound (Cr of Cr in combinations such as welded condition C and Cr
23C
6And Cr
7C
3Deng) and produce poor Cr district, cause these regional erosion resistances significantly to descend.Therefore, it is limited to 0.004～0.012%.
Cr content: Cr is the alloying element that makes ferritic stainless steel have ferritic structure and have good corrosion resistance.Ferritic stainless steel is in Oxidant, and chromium can make and generate chromic oxide (Cr on the stainless surface rapidly
2O
3) passive film.The rustless property of ferritic stainless steel and corrosion proof acquisition are because under the medium effect, chromium has promoted the passivation of steel and made steel keep stablizing the result of passivation attitude.Cr is a solidity to corrosion to ferritic stainless steel performance impact maximum, mainly shows the scale resistance medium of raising steel and the performance of acid chloride medium.Cr also improves the anti-local corrosion of steel, such as the performance of stress corrosion under intergranular corrosion, pitting attack, crevice corrosion and some condition.The toughness of steel, ductility just do not reach enough erosion resistances that middle chrome ferritic is had if be lower than 15.0%, and if above 25.0%, then can descend.Therefore, it is limited to 17.00～22.50%.
The vital role of Mo content: Mo is to improve the anti-spot corrosion and the slit and corrosion resistant performance of ferritic stainless steel, promotes the passivation of ferrochrome exothermic, improves Corrosion Resistance of Stainless Steels.But the Mo too high levels can improve the Sensitivity of Stress Corrosion of the cold rolling attitude of ferritic stainless steel, therefore, it is limited to 1.70～2.50%, be lower than at 1.70% o'clock, solidity to corrosion improves limited, but surpasses at 2.50% o'clock, and the ductility of mother metal and weld, toughness will reduce.
The interpolation of Mn content: Mn can improve the purity of molten stainless steel as deoxidant element, improves the surface quality of cold rolled strip, if but Mn surpasses 0.50%, its easily and S in conjunction with formation dissolvable sulfide MnS, make erosion resistance low, therefore, it is limited to below 0.50%.Preferably, Mn:0.10～0.50%.
Si content: Si is what to add as reductor and strengthening element, if it is just insufficient to be lower than 0.10% its effect, and if surpass 0.50%, then when impelling strength reduced, fusion was not enough in the time of also can making welding.Therefore, it is limited to 0.10～0.50%.
N content: N combines in when welding and Ti as mentioned above, helps the grain refining of welding portion, and improve toughness, ductility thus, for guaranteeing its effect, need contain more than 0.008%, but as contain and surpass 0.02%, also can with Cr in conjunction with erosion resistance is reduced.Therefore, it is limited to 0.008～0.020%.
Ti content: Ti is strong carbonitride generting element, particularly the time forms nitride in welding in the molten bath, and the grain refining of welding portion is played main effect.Learn that from experiment the grain refining of welding portion relies on the content of Ti, N, Cr.The following of Ti content limits the use of 0.20 * 10
-4* (Cr)/(N) represent.In addition, the Ti too high levels can cause stabilization than too high, and the content of precipitated phase can be too much.In addition, also can damage the surface quality of steel plate to a certain extent above the Ti of 0.25% content.The relational expression of Ti and Cr, N has guaranteed the precipitated phase of generation TiN in the process of welding heating with assurance welding zone proportion of equiaxed grain, thereby satisfies welding zone flexible requirement.
Nb content: Nb and C combine, and suppress the carbide of welding portion specially and separate out, and erosion resistance is improved.Surpass 0.45% but add, the ductility of mother metal and welding portion, toughness are destroyed.
O content: O content is more than 0.005%, as surface active element, deepens the penetration of welding metal, helps to improve weldability and from the ductility of the weld part of weld bead shape.But the O amount surpasses 0.010%, has hindered ductility, the toughness of weld on the contrary.Therefore, it is limited to 0.005～0.010%.
(Nb)/(Ti) value is 1.5～4, and the regulation of this value is in order to limit the iptimum relationship between Nb and the Ti, and this relation can not only satisfy the proportion of equiaxed grain of welding zone, also can guarantee the surface quality of mother metal simultaneously.
(Nb+Ti)/(C+N) value is 12～22, and the regulation of this value is for fear of the generation that causes intergranular corrosion in mother metal or welding process owing to separating out of carbonitride.
The ferrite-group stainless steel of heterogeneity is carried out argon tungsten-arc welding without welding material, check its weld tissue, ductility, toughness, the influence that investigation steel product ingredient element causes them.Its result is with traditional viewpoint difference, clear and definite is not that the N content of mother metal is forced down, but it is remained on an appropriate level, add corresponding therewith an amount of Ti, just can make the welding portion tissue realize equiax crystalization and grain refining, therefore, the ductility of weld, toughness can significantly be improved, and, control the situation of separating out by the relation that limits between Cr, N, the Ti.
That is to say that the ferrite-group stainless steel that composition range of the present invention constitutes can be realized the grain refining of welding process such as argon tungsten-arc welding to the mother metal weld, the ductility of weld, toughness also can improve thereupon.
The present invention is directed to a kind of composition of ferritic stainless steel and the requirement of production technique, when design technology, mainly take following technical scheme:
Above-mentioned chemical ingredients is smelted by electric furnace-AOD-VOD three-step approach, can guarantee the purity of molten steel and the content of elements such as C, N;
By heating, the temperature of continuously cast bloom or die casting base is controlled at 1000～1100 ℃, makes the ferritic structure homogenizing, the setting of Heating temperature, its objective is in order to prevent to cause the grain coarsening of continuously cast bloom or strand, influence the mechanics and the surface property of final finished owing to too high temperature; If temperature is low excessively, just can not guarantees the hot rolled finishing temperature and cause the increase of resistance to deformation;
Finish hot rolling more than 800 ℃, higher finishing temperature can partly be eliminated work hardening, hot rolling postcooling;
Finish continuous annealing at 950～1050 ℃ after the hot rolling finish to gauge, the continuous annealing system is 0.5～1.5min/mm, is 0.5～1.5min control annealing time according to every mm thickness annealing time just.Annealing temperature cross low or annealing time too short, causing easily can not perfect recrystallization; And annealing temperature is too high or annealing time is long, causes grain coarsening easily; Carry out pickling after the annealing.
Carry out cold rolling, cold rolling accumulation draft 〉=70% again, guarantee the forming property and the surface quality of final finished.Carry out continuous annealing after cold rolling, annealing temperature is 950～1050 ℃, and the continuous annealing system is 0.5～1.5min/mm, is 0.5～1.5min control annealing time according to every mm thickness annealing time just.Annealing temperature cross low or annealing time too short, causing easily can not perfect recrystallization; And annealing temperature is too high or annealing time is long, causes grain coarsening easily.Carry out pickling after the annealing.
The present invention is directed to of the requirement of water treatment system industry, guarantee to design the solidity to corrosion of steel grade, but distinguish to some extent for control and the C of N by reduction C, N content for ferritic stainless steel welding zone high tenacity; Adopt Nb, Ti bistableization, control hot rolling, Nb, Ti second cold rolling, that aftertreatment technology comes control material separate out mutually, by separate out the TiN second phase particle in the welding zone process of setting, fix N on the one hand, reduce Cr
2N separates out tendency, on the other hand TiN has been increased the ratio of equiax crystal in the welding zone as the forming core particle, thereby has improved the toughness of welding zone.
Compared with prior art, the present invention limits containing stainless composition of molybdenum type ferrite and production technique, make and contain the thick problem of molybdenum type ferrite stainless welding zone solution crystal grain, improve the ductility of welding zone, can satisfy of the requirement of water treatment system industry for ferritic stainless steel welding zone high tenacity.The present invention is the ferrite-group stainless steel without the weld good-toughness of welding material, welding process such as the argon tungsten-arc welding that can consider to fill silk, resistance welding, Laser Welding, plasma arc welding.
Description of drawings
Fig. 1 a and Fig. 1 b are two kinds of Photomicrographs that contain molybdenum type ferritic stainless steel Comparative Examples that do not contain the Ti element, and its tissue is mainly column crystal.
Fig. 2 be contain the Ti element among the embodiment and satisfy composition requirement of the present invention contain the stainless Photomicrograph of molybdenum type ferrite, its tissue is mainly equiax crystal, this tissue helps the welding zone flexible and improves.
The magnification of mark is 50 times among Fig. 1,2.
Embodiment
Below further describe the present invention by specific embodiment.
Embodiment 1
Composition shown in embodiment in the table 11 is also made according to the technology shown in the embodiment in the table 21, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1100 ℃, carry out hot rolling, finishing temperature is 820 ℃, carries out after the hot rolling under 1020 ℃ of temperature, 1.2min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 70%, carries out under 1020 ℃ of temperature after cold rolling, 1.2min/mm pickling is carried out in the annealing of time after the annealing.
Measure ferritic stainless steel cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number that present embodiment obtains according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.57mm, the welding zone Erichsen number is 9.24mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 2
Composition shown in embodiment in the table 12 is also made according to the technology shown in the embodiment in the table 22, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1090 ℃, carry out hot rolling, finishing temperature is 850 ℃, carries out after the hot rolling under 980 ℃ of temperature, 0.7min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 75%, carries out under 980 ℃ of temperature after cold rolling, 0.7min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.89mm, the welding zone Erichsen number is 9.53mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 3
Composition shown in embodiment in the table 13 is also made according to the technology shown in the embodiment in the table 23, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1050 ℃, carry out hot rolling, finishing temperature is 800 ℃, carries out after the hot rolling under 1050 ℃ of temperature, 1.5min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 79%, carries out under 1050 ℃ of temperature after cold rolling, 1.5min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 11.03mm, the welding zone Erichsen number is 9.68mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 4
Composition shown in embodiment in the table 14 is also made according to the technology shown in the embodiment in the table 24, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1000 ℃, carry out hot rolling, finishing temperature is 860 ℃, carries out after the hot rolling under 950 ℃ of temperature, 0.5min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 81%, carries out under 950 ℃ of temperature after cold rolling, 0.5min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.36mm, the welding zone Erichsen number is 9.53mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 5
Composition shown in embodiment in the table 15 is also made according to the technology shown in the embodiment in the table 25, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1095 ℃, carry out hot rolling, finishing temperature is 800 ℃, carries out after the hot rolling under 1050 ℃ of temperature, 1.5min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 80%, carries out under 1050 ℃ of temperature after cold rolling, 1.5min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.89mm, the welding zone Erichsen number is 9.21mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 6
Composition shown in embodiment in the table 16 is also made according to the technology shown in the embodiment in the table 26, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1080 ℃, carry out hot rolling, finishing temperature is 830 ℃, carries out after the hot rolling under 1000 ℃ of temperature, 1.3min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 85%, carries out under 1000 ℃ of temperature after cold rolling, 1.3min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.98mm, the welding zone Erichsen number is 9.86mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 7
Composition shown in embodiment in the table 17 is also made according to the technology shown in the embodiment in the table 27, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1060 ℃, carry out hot rolling, finishing temperature is 820 ℃, carries out after the hot rolling under 1020 ℃ of temperature, 1.2min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 75%, carries out under 1020 ℃ of temperature after cold rolling, 1.2min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.09mm, the welding zone Erichsen number is 9.12mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
Embodiment 8
Composition shown in embodiment in the table 18 is also made according to the technology shown in the embodiment in the table 28, and promptly electric furnace-AOD-VOD three-step approach is smelted, and carries out continuous casting, continuously cast bloom is heated to 1100 ℃, carry out hot rolling, finishing temperature is 850 ℃, carries out after the hot rolling under 980 ℃ of temperature, 0.7min/mm the annealing of time, carry out cold rollingly again, cold rolling draft is 70%, carries out under 980 ℃ of temperature after cold rolling, 0.7min/mm pickling is carried out in the annealing of time after the annealing.
Measure the cold-reduced sheet mother metal Erichsen number and the welding zone Erichsen number of present embodiment again according to GB4156-84 " cupping test of metal method (thickness 0.2～2mm) " method, the result is as shown in table 3, the mother metal Erichsen number is 10.12mm, the welding zone Erichsen number is 9.09mm, and the welding zone of this explanation present embodiment steel plate has good toughness.
In sum, that adopts that composition of the present invention and technology obtained contains molybdenum type ferritic stainless steel, and its welding zone good-toughness goes for occasion higher to the toughness reguirements of steel grade welding zone in the water treatment system industry, has bright development prospect.
Though abovely the present invention is had been described in detail by specific embodiment; but be not limited only to these embodiment; without departing from the inventive concept of the premise; can also more changeableization or improved other embodiment, and these changes and improvements all belong to the claimed scope of the application's claim.
The technology of table 2 embodiment
| Embodiment | Heating temperature (℃) | Hot rolling finishing temperature (℃) | Annealing temperature (℃) | Hot rolling continuous annealing system (min/mm) | Cold rolling accumulative total deformation rate (%) | Annealing temperature (℃) | Cold rolled continuous annealing system (min/mm) |
| 1 | 1100 | 820 | 1020 | 1.2 | 70 | 1020 | 1.2 |
| 2 | 1090 | 850 | 980 | 0.7 | 75 | 980 | 0.7 |
| 3 | 1050 | 800 | 1050 | 1.5 | 79 | 1050 | 1.5 |
| 4 | 1000 | 860 | 950 | 0.5 | 81 | 950 | 0.5 |
| 5 | 1095 | 800 | 1050 | 1.5 | 80 | 1050 | 1.5 |
| 6 | 1080 | 830 | 1000 | 1.3 | 85 | 1000 | 1.3 |
| 7 | 1060 | 820 | 1020 | 1.2 | 75 | 1020 | 1.2 |
| 8 | 1100 | 850 | 980 | 0.7 | 70 | 980 | 0.7 |
The performance of table 3 embodiment
| Embodiment | Mother metal Erichsen number (mm) | Welding zone Erichsen number (mm) |
| 1 | 10.57 | 9.24 |
| 2 | 10.89 | 9.53 |
| 3 | 11.03 | 9.68 |
| 4 | 10.36 | 9.53 |
| 5 | 10.89 | 9.21 |
| 6 | 10.98 | 9.86 |
| 7 | 10.09 | 9.12 |
| 8 | 10.12 | 9.09 |
Annotate: contain the stainless mother metal Erichsen number 〉=10mm of molybdenum type ferrite, welding zone Erichsen number 〉=9mm represents the welding zone good-toughness.
Claims (9)
1. one kind contains the stainless manufacture method of molybdenum type ferrite, comprising:
With the chemical ingredients of weight percent meter be: C:0.004～0.012%, N:0.008～0.020%, (C+N)≤0.030%, Si:0.10～0.50%, Mn≤0.50%, Cr:17.00～22.50%, Mo:1.70～2.50%, Nb:0.15～0.45%, Ti:0.20 * 10
-4* (Cr)/(N)～0.25%, and O:0.005～0.010%, all the other are the composition of unavoidable impurities and balance element of Fe, smelt by electric furnace-AOD-VOD three-step approach;
Continuous casting or die casting;
The temperature that adds thermal control continuously cast bloom or die casting base is 1000～1100 ℃;
Finish hot rolling more than 800 ℃, the hot rolling postcooling;
Hot rolled coil is finished continuous annealing at 950～1050 ℃, carries out pickling after the annealing;
Cold rolling accumulation draft 〉=70% carries out continuous annealing after cold rolling, and annealing temperature is 950～1050 ℃, carries out pickling after the annealing.
2. the stainless manufacture method of molybdenum type ferrite that contains as claimed in claim 1 is characterized in that value (Nb)/(Ti) is 1.5～4; (Nb+Ti)/(C+N) value is 12～22.
3. the stainless manufacture method of molybdenum type ferrite that contains as claimed in claim 1 or 2 is characterized in that Mn:0.10～0.50%.
4. as the arbitrary described stainless manufacture method of molybdenum type ferrite that contains of claim 1～3, it is characterized in that Ti:0.050～0.250%.
5. as the arbitrary described stainless manufacture method of molybdenum type ferrite that contains of claim 1～4, it is characterized in that, finish hot rolling at 800～860 ℃.
6. as the arbitrary described stainless manufacture method of molybdenum type ferrite that contains of claim 1～5, it is characterized in that hot rolled coil continuous annealing system is 0.5～1.5min/mm, promptly every mm thickness heat-up time is 0.5～1.5min.
7. as the arbitrary described stainless manufacture method of molybdenum type ferrite that contains of claim 1～6, it is characterized in that cold rolling accumulation draft is 70～85%.
8. as the arbitrary described stainless manufacture method of molybdenum type ferrite that contains of claim 1～7, it is characterized in that the continuous annealing system after cold rolling is 0.5～1.5min/mm.
9. contain molybdenum type ferrite stainless steel cold-rolled plate as the arbitrary described method manufacturing of claim 1～8.
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| JP2017538862A (en) * | 2014-12-26 | 2017-12-28 | ポスコＰｏｓｃｏ | Ferritic stainless steel |
| CN109355478A (en) * | 2018-12-24 | 2019-02-19 | 东北大学 | Improve the B444M2 type ferritic stainless steel and preparation method thereof of high-temperature oxidation resistance |
| CN112647026A (en) * | 2020-12-25 | 2021-04-13 | 中北大学 | Method for preparing high-chromium and high-molybdenum ferritic stainless steel |
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