CN104046917A - Cu-rich nanocluster reinforced ultra-high strength ferrite steel and manufacturing method thereof - Google Patents
Cu-rich nanocluster reinforced ultra-high strength ferrite steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a Cu-rich nanocluster reinforced ultra-high strength ferrite steel and a manufacturing method thereof. The Cu-rich nanocluster reinforced ultra-high strength ferrite steel comprises the following components by weight: 0-0.2% of C; 0.5-5% of Cu; 0.01-4% of Ni; 0.01-4% of Mn; 0.001-2% of Al; 0-12% of Cr; 0-3% of Mo, 0-3% of W, with the sum of Mo and W being not less than 0.05%; 0-0.5% of V, 0-0.5% of Ti, 0-0.5% of Nb, with the sum of V, Ti and Nb being not less than 0.01%; 0-1% of Si; 0.0005-0.05% of B; not more than 0.04% of P; not more than 0.04% of S; not more than 0.04% of N; not more than 0.05% of O; and the balance Fe and unavoidable impurities. After smelting, casting and forging rolling, solid solution and aging treatment are carried out to prepare nanocluster reinforcement based ferrite steel combining fine grain, solid solution and dislocation strengthening, and the ferrite steel has excellent toughness, weldability and corrosion resistance.
Description
Technical field
The present invention relates to a kind of superstrength ferritic steel and manufacture method thereof, be specifically related to a kind of superstrength ferritic steel and manufacture method thereof of rich Cu nanocluster strengthening.
Background technology
Along with resource, environmental stress strengthen day by day, environmental protection, the energy-conservation attention that is more and more subject to Iron And Steel Industry.The ultrahigh-strength steel of developing energy-conservation, material-saving and excellent performance, meets the structure and function requirement of each Application Areas, is the important channel of realizing sustainable development of iron and steel industry.
Tradition ultrahigh-strength steel, as low-temperaturetempering martensitic stucture or lower bainite build up low alloy steel, high tempering alloy carbide precipitate, secondary hardening build up ultrahigh-strength steel, intermetallic compound precipitation strength maraging steel etc., reached to a certain extent the requirement of superstrength, but high-carbon, high alloy and thermal treatment change the problems such as the characteristics such as rapid cooling make it still have welding property and plasticity and toughness are poor, cost is high, scantling is limited that require.
Development along with nanosecond science and technology, utilize nanometer precipitated phase highly malleablized mechanism to improve the important channel that ultrahigh-strength steel over-all properties has become development of new ultrahigh-strength steel, particularly compare with adopting traditional martensitic matrix, on ferrite structure basis, utilize strengthened nano precipitated phase mechanism development of new ultrahigh-strength steel to there is great technique and cost advantage.Recently, investigator is carrying out preliminary study aspect Cu nanocluster precipitation strength steel.Cu is face-centred cubic structure element, in body-centered cubic structure ferrite matrix, solid solubility is very little, through suitable thermal treatment Cu, can from ferrite matrix, separate out, form Cu nanocluster precipitated phase, produce the intensity that precipitation strength effect improves steel, and research shows that nanocluster size is less, the amount of separating out is more, separate out spacing less, distribute more evenly, precipitating reinforcing effect is better.But the Cu particle size in Cu precipitation strength steel is mostly more than 50nm at present, and the amount of separating out is few, precipitate particle spacing is large, size distribution is uneven, make the strengthening effect of Cu particle limited, the intensity of gained Cu precipitation strength steel is mostly below 1000MPa, as disclosed the precipitation hardened chrome ferritic stainless steel of a kind of nano level Cu in patent CN101328561A, wherein Cu precipitate particle is of a size of 50～200nm, the reinforced ferrite steel yield strength of utilizing Cu phase precipitation strength effect to obtain is not less than 300MPa, tensile strength is not less than 450MPa, elongation is not less than 25%.
The present invention is by kind and content and the thermal treatment process of Reasonable Regulation And Control alloying element, optimize the nucleation and growth process of Cu nanocluster, and then optimize nanocluster separate out size, quantity and distribution, form concentration high, be evenly distributed, rich Cu nanocluster that size is tiny, the farthest strengthening effect of the rich Cu nanocluster of performance, the multiple schedule of reinforcements such as combined with fine-grained strengthening, solution strengthening and dislocations strengthening are simultaneously realized complex intensifying, make the superstrength ferritic steel of the rich Cu nanocluster strengthening of low-carbon (LC), low cost, excellent combination property.
Summary of the invention
An object of the present invention is to provide a kind of superstrength ferritic steel of rich Cu nanocluster strengthening, wherein take high density, be uniformly distributed, size is tiny rich Cu nanocluster strengthening is as main, simultaneously combined with fine-grained strengthening, solution strengthening and dislocations strengthening various ways are realized complex intensifying, make there are ultra-high strength and toughness, the novel low-cost superstrength ferritic steel of superior weldability energy and corrosion resistance nature.
Another object of the present invention is to provide a kind of method of manufacturing the superstrength ferritic steel of above-mentioned rich Cu nanocluster strengthening.
On the one hand, the invention provides a kind of superstrength ferritic steel of rich Cu nanocluster strengthening, by weight percentage, its chemical composition is as follows: C is 0～0.2%; Cu is 0.5～5%; Ni is 0.01～4%; Mn is 0.01～4%; Al is 0.001～2%; Cr is 0～12%; Mo is that 0～3%, W is that 0～3%, Mo+W is not less than 0.05%; V is that 0～0.5%, Ti is that 0～0.5%, Nb is that 0～0.5%, V+Ti+Nb is not less than 0.01%; Si is 0～1%; B is 0.0005～0.05%; P is not higher than 0.04%; S is not higher than 0.04%; N is not higher than 0.04%; O is not higher than 0.05%; Surplus is Fe and inevitable impurity.
In one embodiment of the invention, the component of described rich Cu nanocluster is Cu, Ni, Mn, Al.
In another embodiment of the invention, the mean sizes of described rich Cu nanocluster is 3nm, and average headway is 2～10nm, and every cu μ m nanoclusters number of clusters is not less than 10,000.
In another embodiment of the invention, in the superstrength ferritic steel of described rich Cu nanocluster strengthening, also comprise composite Nano carbide (V, Ti, Nb) C, described nano-carbide is of a size of 5～100nm.
In another embodiment of the invention, the matrix of the superstrength ferritic steel of described rich Cu nanocluster strengthening is ferrite, and described ferritic average grain size is 1～20 μ m.
In another embodiment of the invention, the yield strength of the superstrength ferritic steel of described rich Cu nanocluster strengthening is 900～1200MPa, and tensile strength is 1200～1500MPa, and elongation is 10～20%, and relative reduction in area is 50%～80%.
On the other hand, the present invention also provides a kind of method of manufacturing the superstrength ferritic steel of described rich Cu nanocluster strengthening, and its step is as follows:
(1) make the feedstock composition that the chemical composition of the superstrength ferritic steel of described rich Cu nanocluster strengthening forms carry out successively melting, casting and forging rolling;
(2) carry out solution treatment, be then cooled to room temperature;
(3) carry out ageing treatment, be then cooled to room temperature.
In a kind of embodiment of the inventive method, described solution treatment is carried out within the scope of 800～1300 ℃.
In the another kind of embodiment of the inventive method, described solution treatment is carried out at 900 ℃.
In the another kind of embodiment of the inventive method, described solution treatment is carried out 0.1～3 hour.
In the another kind of embodiment of the inventive method, described solution treatment is carried out 0.5 hour.
In the another kind of embodiment of the inventive method, described ageing treatment is carried out within the scope of 400～600 ℃.
In the another kind of embodiment of the inventive method, described ageing treatment is carried out at 550 ℃.
In the another kind of embodiment of the inventive method, described ageing treatment is carried out 0.1～20 hour.
In the another kind of embodiment of the inventive method, described ageing treatment is carried out 2 hours.
The present invention is by Reasonable Regulation And Control alloying element kind and content and thermal treatment process, obtain concentration high, be evenly distributed, the rich Cu nanocluster that size is tiny, effectively brought into play the precipitation strength effect of nanocluster, and combined with fine-grained strengthening, the various ways such as solution strengthening and dislocations strengthening carries out complex intensifying, obtained excellent obdurability, wherein take rich Cu nanocluster as main strengthening phase, with its precipitation strength, act as topmost schedule of reinforcement, reduced the carbon content in steel, thereby also there are good welding property and plasticity and toughness, in addition appropriate Cr and Al element have been added, can form stable chromic oxide and alumina protective layer, Cu also plays the effect that improves steel erosion resistance in atmosphere and seawater, thereby comprehensively improved the anti-oxidant and corrosion resistance nature of steel.Complex optimum of the present invention alloying element kind and the content of nanocluster strengthening, refined crystalline strengthening, solution strengthening, use minimum, the most rational alloying element, and compare with existing super-strength martensitic steel, can be without quick process for cooling such as quenchings after superstrength ferritic steel of the present invention thermal treatment, production size is larger, and be suitable for continuous casting and rolling and produce, production cost is lower.
In sum, according to the superstrength ferritic steel of rich Cu nanocluster strengthening of the present invention, take described rich Cu nanocluster strengthening as main, and combining nano carbide refined crystalline strengthening, the various ways such as other solid solution alloy element solid solution strengthenings and dislocations strengthening are realized complex intensifying, thereby obtain obdurability and mate splendid performance, and there is good weldability, erosion resistance and cost are low, can be widely used in automobile, naval vessel, bridge, pipeline, the energy, power station, oceanographic engineering, building structure, pressurized vessel, engineering machinery, the field such as freight container and defence equipment.
Accompanying drawing explanation
With reference to following detailed description those skilled in the art, will understand better on of the present invention and address many other feature and advantage by reference to the accompanying drawings, wherein:
Fig. 1 is according to the high-resolution-ration transmission electric-lens photo of rich Cu nanocluster in the matrix of the superstrength ferritic steel NSF104 of the embodiment of the present invention 1 manufacture;
Fig. 2 is according to the high-resolution-ration transmission electric-lens photo of nano-carbide in the matrix of the superstrength ferritic steel NSF104 of the embodiment of the present invention 1 manufacture;
Fig. 3 is according to displaing micro tissue topography's stereoscan photograph of the superstrength ferritic steel NSF104 of the embodiment of the present invention 1 manufacture;
Fig. 4 is according to the superstrength ferritic steel NSF108 of the embodiment of the present invention 1 manufacture and the tensile stress strain curve of compared steel T24.
Embodiment
According to specific embodiment, technical scheme of the present invention is described further below.Protection scope of the present invention is not limited to following examples, enumerates these examples and only for exemplary purpose, does not limit the present invention in any way.
The superstrength ferritic steel that the invention provides a kind of rich Cu nanocluster strengthening, by weight percentage, its chemical composition is as follows: C is 0～0.2%; Cu is 0.5～5%; Ni is 0.01～4%; Mn is 0.01～4%; Al is 0.001～2%; Cr is 0～12%; Mo is that 0～3%, W is that 0～3%, Mo+W is not less than 0.05%; V is that 0～0.5%, Ti is that 0～0.5%, Nb is that 0～0.5%, V+Ti+Nb is not less than 0.01%; Si is 0～1%; B is 0.0005～0.05%; P is not higher than 0.04%; S is not higher than 0.04%; N is not higher than 0.04%; O is not higher than 0.05%; Surplus is Fe and inevitable impurity.
Below the restriction reason of each chemical composition content range in the superstrength ferritic steel of described rich Cu nanocluster strengthening is described:
C: form stable nano-carbide with V, Ti and Nb, can produce precipitation strength effect, effective refinement ferrite crystal grain, produce refined crystalline strengthening effect, thereby improve the intensity of steel, in order to guarantee superior weldability energy and the toughness of steel, only use low carbon content in the present invention, so the present invention is limited to 0～0.2% by the content of C;
Cu: the main component of nanocluster, also be the most important element of nanocluster strengthening in the present invention, utilizing lower-cost Cu to form nanocluster can efficient hardening ferritic steel, reduce carbide reinforced application, and then can reduce the carbon content in steel, contribute to improve welding property and the toughness of steel, in addition Cu also has the effect that improves steel erosion resistance in atmosphere and seawater, when Cu content is lower than 0.5% time, strengthening effect is not obvious, and when Cu too high levels, can produce red brittleness, unfavorable to processing characteristics, therefore the present invention is limited to 0.5～5% by Cu content,
Ni: one of component of nanocluster, participate in nanocluster precipitation strength effect, and can hinder nanocluster and grow up, contributing to refinement nanocluster, Ni also contributes to improve the toughness of steel, yet Ni is austenite former, during its too high levels, in steel, meeting retained austenite, causes tissue odds even, and can increase production cost, so the present invention is limited to 0.01～4% by Ni content;
Mn: one of component of nanocluster, participate in nanocluster precipitation strength effect, Mn is austenite former, has and postpones austenite to the effect of ferritic transformation, is conducive to refinement ferrite crystal grain, improve intensity and toughness, yet during Mn too high levels, in steel, meeting retained austenite, causes tissue odds even, and high Mn content can cause steel billet segregation, toughness variation and weldability to reduce, so the present invention is limited to 0.01～4% by Mn content;
Al: one of component of nanocluster, participates in nanocluster precipitation strength effect, the reductor in Al or steelmaking process, there is the effect of cleaning molten steel, yet during Al too high levels, can bring the difficulty of smelting casting, so the present invention is limited to 0.001～2% by Al content;
Cr: anti-oxidant and anticorrosive element, can improve the anti-oxidant and corrosion resistance nature of steel, while or ferrite former, can increase the ferritic structure with stabilized steel, yet Cr too high levels can reduce the toughness of steel, and can increase production cost, so the present invention is limited to 0～12% by Cr content;
Mo and W: ferrite former, the ferritic structure of stabilized steel, can also play solution strengthening effect, however Mo and W interpolation are too much, and matrix can be separated out Fe
2mo and Fe
2w fragility phase, makes the toughness drop of steel, so the present invention is all limited to 0～3% by the content of Mo and W, and the total amount of Mo and W is not less than 0.05%;
V, Ti and Nb: strong carbon compound forming element, MC type carbide (M:V, Ti or Nb) with C formation face-centred cubic structure, have the advantages that size is little, thermostability is high, can effectively hinder grain growth, the effect of performance refined crystalline strengthening and precipitation strength, in the present invention in order to guarantee superior weldability energy and the toughness of steel, only use low carbon content, V, Ti or the Nb of interpolation 0.5% can make solid carbon effect reach capacity, therefore the present invention is all limited to 0～0.5% by the content of V, Ti and Nb, and the total amount of V, Ti and Nb is not less than 0.01%;
Si: improve carbon and distribute, prevent the formation of cementite, ferritic structure that can also stabilized steel, plays solution strengthening effect, however Si add when too much, can reduce the toughness of steel, so the present invention is limited to 0～1% by Si content;
B: can significantly purify crystal boundary, improve intensity and the toughness of steel, yet during B too high levels, crystal boundary can be separated out too much boride, reduce the toughness of steel, so the present invention be limited to 0.0005～0.05% by B content;
P and S: inevitable impurity element in steel, when content is high, can form frangible compounds with Cu, toughness and the welding property of harm steel, so the content of P and S is all controlled at below 0.04%;
N and O: inevitable impurity element in steel, toughness and the welding property of harm steel, so the content of N and O is controlled at respectively below 0.04% and 0.05%;
Composition beyond above-mentioned is Fe and other inevitable impurity, in not damaging the scope of effect of the present invention, does not get rid of and also contains above-mentioned composition in addition.
The present invention also provides a kind of method of manufacturing the superstrength ferritic steel of described rich Cu nanocluster strengthening, and its step is as follows:
(1) make the feedstock composition that the chemical composition of the superstrength ferritic steel of described rich Cu nanocluster strengthening forms carry out successively melting, casting and forging rolling;
(2) carry out solution treatment, be then cooled to room temperature;
(3) carry out ageing treatment, be then cooled to room temperature.
The method according to this invention, can be in electric arc furnace, converter, in induction furnace, smelt, then can adopt continuous casting mode to produce strand or adopt die casting mode to produce ingot casting, described strand or ingot casting have good cold, hot workability, then can carry out cold rolling, warm-rolling or forge or hot rolling within the scope of 800～1300 ℃, through rolling or after forging, sheet material is carried out within the scope of 800～1300 ℃ to solution treatment, treatment time is 0.1～3 hour, cooling subsequently, the type of cooling can be air cooling, air-cooled, oil quenching or shrend, can be cooled to room temperature or directly be cooled to aging temp and carry out ageing treatment, ageing treatment is carried out within the scope of 400～600 ℃, treatment time is 0.1～20 hour, cooling subsequently, the type of cooling can be air cooling equally, air-cooled, oil quenching or shrend, finally obtain the superstrength ferritic steel of rich Cu nanocluster strengthening of the present invention.
The present invention is by cold and hot deformation techniques such as forging rollings, can crystal grain thinning, also can introduce the defects such as a large amount of dislocations and room, and for highly concentrated nano cluster nucleation provides good condition, also can realize dislocations strengthening.According to the present invention, heat-treat subsequently, under specified temp, successively carry out solution treatment and the ageing treatment of certain time length, through solution treatment, obtain ferrite supersaturated solid solution, by reasonable control aging temp and aging time, effectively control separating out of nanocluster and grow up.With regard to solution treatment, Cu element has very large solid solubility in the austenite of face-centred cubic structure, according to the present invention, at 800～1300 ℃, carry out solution treatment, can guarantee added Cu element completely solid solution among matrix, excess Temperature crystal grain is seriously alligatoring, and the intensity of steel and toughness all can decline.With regard to ageing treatment, the solid solubility of Cu element in ferrite is very low, and solid solubility can decline with the decline of temperature, if adopt too high aging temp, nanocluster will alligatoring, if adopt too low aging temp, nanocluster is separated out deficiency.According to the present invention after above-mentioned solution treatment again after 400～600 ℃ are carried out ageing treatment, through high-resolution-ration transmission electric-lens photo, confirm, in ferrite matrix coherence separated out concentration high, be evenly distributed, rich Cu nanocluster that size is tiny.According to strengthened nano precipitated phase mechanism, dislocation and precipitated phase interaction, precipitated phase effectively hinders dislocation moving, thereby realize, strengthens, many in precipitated phase quantity, size is little, can obtain maximum strengthening effect be evenly distributed in the situation that.The present invention by Reasonable Regulation And Control alloy element and thermal treatment process obtain concentration high, be evenly distributed, rich Cu nanocluster that size is tiny, brought into play to greatest extent the strengthening effect of rich Cu nanocluster.In addition, in the present invention, except Cu element, also having other element (Ni, Mn and Al) is also the important composition of nanocluster, not only affects the nucleation of nanocluster, and can hinder nanocluster and grow up, and contributes to refinement nanocluster.
In addition, in the superstrength ferritic steel of rich Cu nanocluster strengthening of the present invention, also comprise carbide forming element (V, Ti and Nb) and trace carbon element (C), after above-mentioned thermal treatment, in ferrite matrix, with interface emission form, separate out a small amount of composite Nano carbide, in the situation that not endangering welding property and toughness, the nano-carbide that these are tiny, thermostability is high has played refined crystalline strengthening effect.The present invention is simultaneously by optimizing various alloying element kinds and content, actively brought into play the solution strengthening effect of alloying element (for example Mo and W), and by rational cold and hot distortion and thermal treatment process, realized dislocations strengthening, thereby reach, take the strengthening of rich Cu nanocluster and realize the effect of complex intensifying as main and combined with fine-grained strengthening, solution strengthening and dislocations strengthening.
Unless be separately construed as limiting, term used herein is the implication that those skilled in the art understand conventionally.
Below in conjunction with accompanying drawing, by embodiment, the present invention is described in further detail.
Embodiment 1
According to the present invention, the compositing range of the superstrength ferritic steel of rich Cu nanocluster strengthening, has smelted 9 kinds of invention steel NSF101～109, has smelted the T24 steel of power plant application as a comparison simultaneously.According to the alloying constituent of NSF101～109 shown in table 1 and T24, form, in arc-melting furnace, smelt and cast, the ingot casting making is rolled to processing with each 5～10% draught, obtain the sheet material that total deformation is 70% left and right.Sheet material after rolling is carried out at 900 ℃ to solution treatment in 0.5 hour, in argon gas quenching mode, be cooled to room temperature subsequently, then at 550 ℃, carry out 2 hours ageing treatment, in argon gas quenching mode, be cooled to room temperature equally subsequently, thereby make invention steel NSF101～109 and compared steel T24.
The alloying constituent of table 1. invention steel NSF101～109 and compared steel T24 forms
Embodiment 2
According to the alloying constituent of NSF104 in table 1, form, in arc-melting furnace, smelt and cast, the ingot casting making is rolled to processing with each 5～10% draught, obtain the sheet material that total deformation is 70% left and right.Sheet material after rolling is carried out at 850 ℃ to solution treatment in 0.5 hour, in shrend mode, be cooled to room temperature subsequently, then at 550 ℃, carry out 2 hours ageing treatment, in air cooling mode, be cooled to room temperature subsequently.Thereby make invention steel NSF104 '.
Embodiment 3
According to the alloying constituent of NSF104 in table 1, form, in arc-melting furnace, smelt and cast, the ingot casting making is rolled to processing with each 5～10% draught, obtain the sheet material that total deformation is 70% left and right.Sheet material after rolling is carried out at 1200 ℃ to solution treatment in 0.5 hour, in shrend mode, be cooled to room temperature subsequently, then at 550 ℃, carry out 2 hours ageing treatment, in air cooling mode, be cooled to room temperature subsequently.Thereby make invention steel NSF104 ".
Test example 1
Compared steel T24 after utilizing transmission electron microscope to above-mentioned thermal treatment and invention steel NSF101～109 are analyzed.As shown in Table 1, during compared steel T24 forms, containing nanocluster forming element, in transmission electron microscope results display comparison steel T24, there is not nanocluster, and in invention steel NSF101～109, found that concentration is high, be evenly distributed, rich Cu nanocluster that size is tiny.Fig. 1 is the high-resolution-ration transmission electric-lens photo of nanocluster in invention steel NSF104 matrix, wherein the mean sizes of nanocluster is about 3nm, be evenly distributed, average headway is about 4nm, every cu μ m nanoclusters number of clusters is no less than 10,000, by transmission electron microscope energy spectrum analysis, to determine, nanocluster mainly comprises Cu, Ni, Mn and Al element.As can be seen here, rich Cu nanocluster according to the present invention strengthen in low-cost superstrength ferritic steel, formed concentration high, be evenly distributed, rich Cu nanocluster that size is tiny, according to strengthened nano precipitated phase mechanism, the rich Cu nanocluster that these concentration are high, size is little effectively hinders dislocation motion, can significantly strengthen the intensity of ferritic steel.
In addition, utilize transmission electron microscope also to observe some nano-carbides, Fig. 2 is the high-resolution-ration transmission electric-lens photo of the nano-carbide of separating out in invention steel NSF104 matrix, by transmission electron microscope energy spectrum analysis, determine, described nano-carbide is composite Nano carbide (V, Ti) C, is of a size of about 20nm.Nano-carbide has the advantages that size is little, thermostability is high, has effectively hindered grain growth, plays refined crystalline strengthening effect.In addition, compare with simple carbide, double carbide has slower coarsening behavior, thereby has better thermostability.Fig. 3 is the stereoscan photograph of invention steel NSF104 displaing micro tissue topography, wherein matrix is fine ferrite grain as shown in the figure, even grain size, tiny, average grain size is 1.5 μ m, the above-mentioned nanometer precipitated phase of separating out in visible matrix has effectively played the effect of crystal grain thinning, known according to Hall-Petch relational expression, by refining grain size, can improve the strength of materials, grain-size is less simultaneously, plasticity is better, and toughness index is higher.
Test example 2
By line, cut tension specimen is processed into in invention steel NSF101～109 and compared steel T24, carry out tensile test at room temperature on MTS trier, yield strength, tensile strength, relative reduction in area and elongation the results are shown in table 2.Fig. 4 is invention steel NSF108 constructed in accordance and the tensile stress strain curve of compared steel T24.From table 2 and Fig. 4, compared steel T24 is after identical smelting and thermal treatment process, and its yield strength is 347MPa, tensile strength is 586MPa, conform to the document of having delivered, and invention steel NSF101～109 constructed in accordance, yield strength is 900～1200MPa, tensile strength is 1200～1500MPa, compare with T24 steel, yield strength and tensile strength all obviously improve, and relative reduction in area remains on 50%～80%, elongation remains on 10～20%, obdurability good match.As can be seen here, the present invention passes through to adjust nanocluster strengthening, refined crystalline strengthening and solution strengthening element, and takes suitable thermal treatment process, has significantly improved the intensity of steel.
The room temperature tensile mechanical property of table 2. invention steel NSF101～109 and compared steel T24
| Numbering | Yield strength (MPa) | Tensile strength (MPa) | Relative reduction in area (%) | Elongation (%) |
| NSF101 | 942 | 1201 | 68 | 13.2 |
| NSF102 | 1124 | 1264 | 64 | 13.7 |
| NSF103 | 1062 | 1357 | 60 | 13.6 |
| NSF104 | 1042 | 1261 | 66 | 14.2 |
| NSF105 | 1057 | 1354 | 59 | 10.7 |
| NSF106 | 1124 | 1245 | 62 | 13.5 |
| NSF107 | 972 | 1210 | 72 | 16.6 |
| NSF108 | 1119 | 1448 | 55 | 13.5 |
| NSF109 | 1141 | 1266 | 61 | 13.1 |
| T24 | 347 | 586 | 89 | 22.9 |
Test example 3
By line, cut the invention steel NSF104 ' making in embodiment 2 is processed into tension specimen, carry out tensile test at room temperature on MTS trier, recording yield strength is 1082MPa, and tensile strength is 1240MPa, and relative reduction in area is 67%, and elongation is 12.4%.
As described in Example 2, the alloying constituent of invention steel NSF104 ' and NSF104 form and thermal treatment process identical, difference is, invention steel NSF104 ' carries out solution treatment at 850 ℃.By reducing solid solution temperature, can prevent that crystal grain from growing up fast, obtain fine grained texture.Thereby, the mechanical property being recorded from above-mentioned tensile tests at room, the superstrength ferritic steel that carries out the rich Cu nanocluster strengthening that solution treatment makes at described temperature has the intensity of superelevation and good plasticity and toughness equally.
Test example 4
By line, cut by the invention steel NSF104 making in embodiment 3 that " be processed into tension specimen, carry out tensile test at room temperature on MTS trier, recording yield strength is 944MPa, and tensile strength is 1207MPa, and relative reduction in area is 62%, and elongation is 12.7%.
As described in Example 3, invention steel NSF104 " form with the alloying constituent of NSF104 and thermal treatment process identical, difference is, invention steel NSF104 " carries out solution treatment at 1200 ℃.By improving solid solution temperature, make the abundant solid solution of alloying element, cooling rear alloying element will have larger degree of supersaturation in ferrite matrix, thereby increases the nucleation rate of nanometer precipitated phase, and then can produce more nano-strengthening phase when ageing treatment.Thereby, the mechanical property being recorded from above-mentioned tensile tests at room, the superstrength ferritic steel that carries out the rich Cu nanocluster strengthening that solution treatment makes at described temperature has the intensity of superelevation and good plasticity and toughness equally.
In sum, one aspect of the present invention is from thermodynamics optimization design alloying constituent, rationally adjust the proportioning of face-centered cubic element, C element and other alloying elements, farthest increase the volume fraction of nanometer precipitated phase, and control Precipitation Temperature simultaneously and separate out the time, bring up a large amount of nucleation sites, whole solid solution alloy elements are evenly separated out, and control growing up of nanometer precipitated phase while separating out in position, obtain concentration high, be evenly distributed, rich Cu nanocluster that size is tiny, to realizing the superstrength of novel ultra-high strength steel, play the effect of most critical.In addition the effective crystal grain thinning of nano-carbide, optimized alloy element produces the effect of solution strengthening, and cold and hot distortion produces crystal grain thinning and dislocations strengthening effect.Therefore, the superstrength ferritic steel of rich Cu nanocluster strengthening of the present invention is to take nanocluster strengthening as main, NEW TYPE OF COMPOSITE reinforced low-carbon, low-cost ultrahigh-strength steel that the various ways such as refined crystalline strengthening, solution strengthening and dislocations strengthening combine, there is superstrength and good welding property, plasticity and toughness, erosion resistance, excellent combination property, can be widely used in the fields such as automobile, naval vessel, bridge, pipeline, the energy, power station, oceanographic engineering, building structure, pressurized vessel, engineering machinery, freight container and defence equipment.
Those skilled in the art it should be noted in the discussion above that embodiment described in the invention is only exemplary, can make within the scope of the invention various other replacements, changes and improvements.Thereby, the invention is not restricted to above-mentioned embodiment, and be only defined by the claims.
Claims (18)
1. the superstrength ferritic steel that rich Cu nanocluster is strengthened, by weight percentage, its chemical composition is as follows:
C is 0～0.2%; Cu is 0.5～5%; Ni is 0.01～4%; Mn is 0.01～4%; Al is 0.001～2%; Cr is 0～12%; Mo is that 0～3%, W is that 0～3%, Mo+W is not less than 0.05%; V is that 0～0.5%, Ti is that 0～0.5%, Nb is that 0～0.5%, V+Ti+Nb is not less than 0.01%; Si is 0～1%; B is 0.0005～0.05%; P is not higher than 0.04%; S is not higher than 0.04%; N is not higher than 0.04%; O is not higher than 0.05%; Surplus is Fe and inevitable impurity.
2. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of claim 1, the component of described rich Cu nanocluster is Cu, Ni, Mn, Al.
3. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of claim 1, the mean sizes of described rich Cu nanocluster is 3nm, and spacing is 2～10nm, and every cu μ m nanoclusters number of clusters is no less than 10,000.
4. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of claim 1, wherein also comprise composite Nano carbide (V, Ti, Nb) C, described composite Nano carbide (V, Ti, Nb) C is of a size of 5～100nm.
5. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of claim 1, its matrix is ferrite, and described ferritic average grain size is 1～20 μ m.
6. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of any one in claim 1 to 5, its yield strength is 900～1200MPa.
7. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of any one in claim 1 to 5, its tensile strength is 1200～1500MPa.
8. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of any one in claim 1 to 5, its elongation is 10～20%.
9. according to the superstrength ferritic steel of the rich Cu nanocluster strengthening of any one in claim 1 to 5, its relative reduction in area is 50%～80%.
10. a method for the superstrength ferritic steel that the rich Cu nanocluster of the aforementioned any one claim of manufacture is strengthened, its step is as follows:
(1) make the feedstock composition that the chemical composition of the superstrength ferritic steel of described rich Cu nanocluster strengthening forms carry out successively melting, casting and forging rolling;
(2) carry out solution treatment, be then cooled to room temperature;
(3) carry out ageing treatment, be then cooled to room temperature.
11. according to the method for claim 10, and wherein said solution treatment is carried out within the scope of 800～1300 ℃.
12. according to the method for claim 11, and wherein said solution treatment is carried out at 900 ℃.
13. according to the method for claim 11 or 12, and wherein said solution treatment is carried out 0.1～3 hour.
14. according to the method for claim 13, and wherein said solution treatment is carried out 0.5 hour.
15. according to the method for claim 10, and wherein said ageing treatment is carried out within the scope of 400～600 ℃.
16. according to the method for claim 15, and wherein said ageing treatment is carried out at 550 ℃.
17. according to the method for claim 15 or 16, and wherein said ageing treatment is carried out 0.1～20 hour.
18. according to the method for claim 17, and wherein said ageing treatment is carried out 2 hours.
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| CN201310081053.6A CN104046917B (en) | 2013-03-13 | 2013-03-13 | Superhigh intensity ferritic steel and the manufacture method thereof of rich Cu nanocluster strengthening |
| PCT/CN2014/073406 WO2014139453A1 (en) | 2013-03-13 | 2014-03-13 | Ultrahigh strength ferritic steel strengthened by using cu-rich nanoclusters, and manufacturing thereof |
| JP2015561927A JP6584961B2 (en) | 2013-03-13 | 2014-03-13 | Copper-rich nanocluster reinforced ultra high strength ferritic steel and method for producing the same |
| JP2019011574A JP6794479B2 (en) | 2013-03-13 | 2019-01-25 | Copper-rich nanocluster reinforced ultra-high-strength ferritic steel and its manufacturing method |
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Also Published As
| Publication number | Publication date |
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| JP2016514211A (en) | 2016-05-19 |
| WO2014139453A1 (en) | 2014-09-18 |
| JP2019094568A (en) | 2019-06-20 |
| JP6584961B2 (en) | 2019-10-02 |
| CN104046917B (en) | 2016-05-18 |
| JP6794479B2 (en) | 2020-12-02 |
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