CN101538686B - Martensite precipitation hardening stainless steel for structural member and manufacturing method thereof - Google Patents
Martensite precipitation hardening stainless steel for structural member and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides a martensite precipitation hardening stainless steel for structural member and a manufacturing method thereof. The martensite precipitation hardening stainless steel comprises the following chemical components in percentage by weight: less than or equal to 0.05 percent of C, 13.50 to 15.50 percent of Cr, 2.5 to 4.0 percent of Cu, 3.0 to 5.0 percent of Ni, 0.15 to 0.40 percent of Nb and Ta, 0.010 to 0.040 percent of N, 0.050 to 0.15 percent of V, less than or equal to 0.80 percent of Si, less than or equal to 1.00 percent of Mn, less than or equal to 0.025 percent of P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities. The stainless steel is smelted by combining an electric furnace, AOD refining and vacuum self-consuming technology, so the stainless steel has the characteristics of high strength, good plasticity, good corrosion resistance and the like, and can meet the requirements of high-strength components such as high-pressure values, oil drill, efficient heavy-duty machinery and the like on material performance.
Description
Technical field
The present invention relates to stainless material, specifically, the present invention relates to Martensite Stainless Steel, more particularly, the present invention relates to a kind of martensitic precipitation that is used for engineering materials.
Background technology
Martensite Stainless Steel is the stainless steel that can adjust its performance through thermal treatment.Difference according to steel interalloy element; Can Martensite Stainless Steel be divided into martensitic chromium stainless steel and martensitic chromium nickel and stainless steel, the martensitic chromium nickel and stainless steel can be divided into common martensitic chromium nickel and stainless steel, martensitic precipitation and martensite aged stainless steel again.Martensitic precipitation has characteristics such as HS, excellent toughness and superior corrosion resistance, and such steel is widely used in the HS forging, have fields such as the high-pressure system valve part that good corrosion resistance requires, efficient heavy-duty machinery parts.
The martensitic precipitation that China generally uses at present is 0Cr17Ni4Cu4Nb, and its chemical ingredients is seen table 1.What this steel adopted is to hang down C, high Cr and contain Cu; Its intensity, toughness, solidity to corrosion are better than general Martensite Stainless Steel; But the use characteristics relative mistake some, mainly be that δ-ferritic existence can influence the thermoplasticity of steel owing to contain δ-ferritic of 5～10% (ferritic that high temperature forms down) in this steel; Reduce the intensity of steel and worsen the transverse toughness of steel, also reduce the corrosion resistance nature of steel simultaneously.
The chemical ingredients (wt%) of the existing martensitic precipitation of table 1 China
| Standard/trade mark | C | Si | Mn | P | S | Cr | Ni | Cu | Nb |
| ?GB/T1220-1999 ?0Cr17Ni4Cu4Nb? | ?≤ ?0.07? | ?≤ ?1.0? | ?≤ ?1.0 | ?≤ ?0.035 | ?≤ ?0.030 | 15.5 ?/ ?17.5 | 3.0 ?/ ?5.0 | 3.0 ?/ ?5.0 | 0.15 ?/ ?0.45 |
The ME of above-mentioned martensitic precipitation 0Cr17Ni4Cu4Nb is to adopt electric furnace+external refining (AOD) to smelt; Cast ∮ 510mm electrode bar, esr becomes ∮ 660mm ESR ingot, forges to become a useful person or cogging; Reroll and process material, forge maximum specification≤∮ 300mm.Following problem appears in this steel in process of production easily: 1) owing to have δ-ferritic in this steel; When hot-work; Austenite and δ-ferritic distortion is inconsistent, makes the surface cracking occur easily, for preventing cracking; Must adopt small deformation amount, many fire to forge (heat → forge → melt down reheat, circulation primary is called a fire) during forging; 2) this steel is relatively more responsive to Heating temperature and soaking time.If Heating temperature is too high or long in the high temperature section soaking time, be easy to make δ-ferrite content to increase, not only influence forgeability, also influence the lateral performance of steel simultaneously, promptly reduce horizontal expansion rate, relative reduction in area, impelling strength etc.
Through retrieval, there are following domestic and international patent documentations to relate to this type of steel grade, its chemical ingredients is seen table 2.
The chemical ingredients (wt%) of the martensitic precipitation that relates in some patent documentations of table 2
| Patent application publication number | C | Cr | Mo | Ti | Al | Cu | Ni | W | B | Nb+Ta |
| ?US20050126662 | ≤ 0.02 | 11.00～ 12.50 | 1.00～ 2.50 | 0.15～ 0.50 | 0.70～ 1.50 | 0.5～ 2.5 | 9.0～ 11.0 | ≤ 2.0 | ≤ 0.001 | |
| ?CN1121962 | ≤ 0.06 | 12.00～ 14.00 | 1.00～ 3.00 | ≤ 0.50 | 0.80～ 1.30 | 7.00～ 9.00 | ≤ 0.50 * | |||
| ?CN1528937 | ≤ 0.06 | 11.00～ 16.50 | 0.50～ 2.00 | ＜ 0.15 | 3.50～ 6.00 |
The steel grade that US 20050126662 relates to is a kind of Mo ultralow-carbon martensitic PH Stainless Steel, and it is to rely on multiple elements compounding ageing strengthenings such as Al, Ti, Cu, W, Mo; It is that CN1121962 and the disclosed steel grade of CN1528937 also all belong to PH Stainless Steel that China applies for a patent publication number, and they are to lean on precipitation strengths such as Mo, Al, Ti.All added precious metal Mo in these disclosed steel grades, increased material cost, and Ni content is higher, be prone to enlarge the austenite phase region of steel.
In order to overcome the above problems, the present inventor has carried out the research of chemical ingredients proportioning and smelting technology, has designed a kind of martensite precipitation hardening stainless steel for structural member with HS, good plasticity, thereby has accomplished the present invention.
One object of the present invention is to provide a kind of martensite precipitation hardening stainless steel for structural member.
Another object of the present invention is to provide the method for manufacture of this martensitic precipitation.
Summary of the invention
First aspect of the present invention provides a kind of martensite precipitation hardening stainless steel for structural member; The chemical ingredients of this martensitic precipitation comprises: C≤0.05wt%, Cr:13.50～15.50wt%, Cu:2.5～4.0wt%, Ni:3.0～5.0wt%, Nb+Ta:0.15～0.40wt%, N:0.010～0.040wt%, V:0.050～0.15wt%, Si≤0.80wt%, Mn≤1.00wt%, P≤0.025wt%, S≤0.010wt%, surplus is Fe and unavoidable impurities.
Below, the chemical ingredients of martensite precipitation hardening stainless steel for structural member of the present invention is done as being described in detail.
C: carbon is austenite former.In Martensite Stainless Steel, along with the increase of carbon content, the intensity and the hardness of steel improve thereupon, but also are accompanied by disadvantageous effects such as solidity to corrosion descends, toughness reduces, welding difficulty because the carbon of too high amount easily with steel in Cr formation Cr
23C
6, the corrosion resisting property of reduction steel.Therefore, in PH Stainless Steel, carbon content generally is no more than 0.10wt%, and carbon content is controlled to be≤0.05wt% in the stainless steel of the present invention.
The effect of N:N and C is similar, can improve the intensity of steel, but solidity to corrosion is not exerted an influence, and can also improve solidity to corrosion in some cases.The addition of N is below 0.04wt% in the general martensitic chromium nickel and stainless steel; Because N belongs to austenite former; In order to keep martensitic stucture, therefore to consider the proportioning of austenite former and ferrite former, if N content was controlled low then do not had strengthening effect.N content of the present invention generally is controlled at 0.010～0.040wt%.
Ni: content can not be too high in the martensitic chromium nickel and stainless steel for nickel, enlarges austenite phase region and the effect that reduces Ms (martensite formation temperature) because nickel element has, if the Ni too high levels makes steel become single-phase austenite easily and loses quenching capacity.Another vital role of Ni is the δ-ferrite content that reduces in the steel, helps improving the toughness, particularly transverse toughness of steel, but also can improve the corrosion resisting property of steel in reducing medium.Therefore, the stainless Ni content of the present invention should be controlled within 3.00～5.00wt% and be advisable.
Cr:Cr is a ferrite former.In Martensite Stainless Steel, Cr content is high, and ferrite content increases in the steel, and the Cr content in the steel of the present invention is lower than the 0Cr17Ni4Cu4Nb steel grade, makes ferrite content reduction in the steel, helps obtaining the little high-performance steel of vertical, horizontal performance difference.On the other hand, for guaranteeing the corrosion resisting property of martensitic precipitation, Cr content should be not less than 12wt%.So the present invention controls Cr content between 13.50～15.50wt%.
Cu:Cu is a kind of austenite former.In general chromium nickel stainless steel, Cu can improve the solidity to corrosion of steel in reducing medium, in martensitic precipitation; The Cu element is in ag(e)ing process; Can form phase between a kind of tiny, a particulate metal that disperse distributes, this intermetallic intensity that makes steel of being on good terms increases, but toughness does not reduce; But the too much adding of Cu becomes difficult relatively with the hot workability that makes steel.So the stainless Cu content of the present invention is preferably 2.5-4.0wt%.
Nb+Ta, V:Nb, V are the strong carbide forming elements.In steel, form the carbide of MC type with carbon, disperse is distributed on the martensitic matrix, and the intensity of steel is improved, and V also has the effect of crystal grain thinning in steel.Because V, Nb are ferrite formers, so V, Nb will be controlled in certain scope in the present invention, Nb+Ta content is controlled at 0.15-0.40wt%, V content is controlled at 0.05-0.15wt%.
Si, Mn, P, S:Si, Mn generally are controlled at≤1.00wt% in common Martensite Stainless Steel, in this scope, change, and to the not obviously influence of tissue of Martensite Stainless Steel, but a certain amount of Si of adding, Mn can play desoxydatoin in steel.In addition, the avidity of Mn and S is strong, can form MnS, helps going in the steel S.Consider the effect of Si, Mn, the present invention generally controls Si≤0.80wt%, Mn≤1.00wt%.S, P belong to impurity element for general purpose steel, and content is low more good more, and the S too high levels will reduce the thermoplasticity and the lateral performance of steel.The characteristics of design mix according to the present invention; To obtain the steel that the vertical, horizontal performance difference is little, use characteristics is good exactly; So S, P content must hang down control; Common Martensite Stainless Steel control P≤0.035wt%, S≤0.020wt%, but stainless steel of the present invention is controlled P≤0.025wt%, S≤0.010wt%.
Second aspect of the present invention provides a kind of method of manufacture of martensite precipitation hardening stainless steel for structural member, and this making method comprises smelting, annealing, heating, forging, annealing operation again, and electric furnace, AOD refining and vacuum consumable technology are adopted in wherein said smelting.
In a preferred implementation: in said AOD refining process, in prereduction slag charge and reduction slag charge, add Al ingot or Ti-Te alloy, terminal point C is controlled at 0.02wt% after the oxygen blast, and before the tapping of AOD stove, adds the Nb-Te alloy.
In a preferred implementation: the speed of melting in the said vacuum consumable technology is 6～8Kg/min,, electrode weight begins to bind when remaining 200～300Kg, and be 50～100Kg to smelting end electrode residuals weight.
In a preferred implementation: the steel ingot shove charge annealing after the smelting, 820～860 ℃ of annealing temperatures, soaking time >=10h, stove are as cold as 500 ℃ of air coolings of coming out of the stove
In a preferred implementation: in said heating process, steel ingot is warmed up to 800～850 ℃ by 40～50 ℃/h again in 500～600 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1200 ± 10 ℃ by 70～80 ℃/h subsequently again, insulation 3.5～5h.
In a preferred implementation: it is 1100～1170 ℃ that the opening of said forging process forged temperature, finishing temperature >=850 ℃.
In a preferred implementation: in said annealing process again, 620～680 ℃ of annealing temperatures, soaking time >=48h is cooled to 550 ℃ of air coolings of coming out of the stove by 20 ℃/h.
The manufacturing process flow of martensitic precipitation of the present invention is: according to chemical ingredients proportioning → employing electric furnace+external refining (AOD) smelting → cast Φ 510mm (or Φ 760mm) electrode → consumable remelting Φ 610mm (or the Φ 810mm) consumable ingot → steel ingot annealing → hammer cogging of steel of the present invention or become a useful person → anneal.
In the method for manufacture of martensitic precipitation of the present invention, following to the processing parameter control principle analysis of key step:
1, smelting technology
(1) electric furnace: in order to satisfy composition of the presently claimed invention, promptly P≤0.025wt%, S≤0.010wt% must select the starting material that hang down S, P for use.
(2) AOD: for the electrode bar carbon content that guarantees cast gets into the control specification, terminal point C is controlled at 0.02wt% after the oxygen blast.For reducing the oxidation of Nb element, must guarantee that deoxidation is good in the steel, so in prereduction slag charge and reduction slag charge, all will add Al ingot or Ti-Te alloy; For preventing to form the inclusion of Nb; Also need add the Nb-Te alloy during smelting, not add metal niobium, and before the tapping of AOD stove, add.
(3) cast: oxidized for preventing molten steel, adopt Ar gas shiled cast.Cast is steady, and the later stage is strengthened feeding, guarantees the electrode bar quality.
(4) vacuum consumable technology: even, fine and close for guaranteeing consumable ingot crystal structure, the average molten speed of control is 6～8Kg/min, and surplus 200～300Kg begins to bind when electrode weight, smelts and finishes electrode residuals weight 50～100Kg.
2, forging process
(1) heating: the characteristics of poor temperature uniformity during, low temperature low according to the stainless steel thermal conductivity; The present invention produces crack due to thermal stress for preventing steel ingot in heat-processed when formulating the heating process of steel, take following method heating: promptly steel ingot is in 500～600 ℃ of needs preheating 2.5h; Be warmed up to 800～850 ℃ by 40～50 ℃/h then; Be incubated 2h again, purpose guarantees that exactly temperature is even, improves the thermal conductivity of steel.The back heat conductivility improves because temperature raises, so can suitably improve heat-up rate, is warmed up to 1200 ± 10 ℃ by 70～80 ℃/h again, is incubated 3.5～5h then (if Φ 610mm steel ingot is incubated 3.5 ± 0.5h; If Φ 810mm large steel ingot, soaking time rises to 5h.), guarantee that the steel ingot internal and external temperature is consistent.
(2) forge: opening and forging temperature is 1100～1170 ℃, and steel is single-phase austenite in this TR, and working plasticity is good, and >=850 ℃ of finishing temperature controls because if finishing temperature is low, exceed the optimal heat plastic zone, are easy to generate forging crack.
Φ 250～Φ 400mm circle forging rod produced by employing Φ 610mm consumable ingot or employing Φ 810mm consumable ingot is produced Φ 300～Φ 600mm circle forging rod, and necessary upsetting pull could guarantee that the lateral performance (intensity, elongation, relative reduction in area etc.) of steel is qualified.The so-called group finger steel ingot of upsetting heats laterally forging of back, forges half of original height, and then vertically is swaged to the original length.
3, annealing process again: martensitic precipitation is relatively more responsive to crackle, must carry out anneal after the forging.The annealing process of steel of the present invention refills furnace annealing for forging the back air cooling, and purpose is to guarantee that austenite is transformed into martensite fully, if forge the back annealing of shove charge at once; The steel temperature is high, and also residual in the tissue have a not austenite of transformation, and retained austenite produces internal stress greatly because of the coefficient of expansion in the steel; When this internal stress is higher than the ys of steel; Crackle will appear in steel inside, need stay for some time after therefore forging, and guarantees that martensitic transformation is complete.Annealing temperature is controlled at 620～680 ℃, and soaking time >=48h is cooled to 550 ℃ of air coolings of coming out of the stove by 20 ℃/h.
Beneficial effect of the present invention is:
1, compares with existing steel grade 0Cr17Ni4Cu4Nb; The chemical ingredients reasonable ratio of martensitic precipitation of the present invention: at first; Reduce the content of chromium element, reduced ferrite content in the steel like this, helped improving horizontal plastic property, the relative reduction in area of steel; Impelling strength reduces the difference between performance in length and breadth.Secondly, reduced C content, increased N and V, thereby do not influenced the intensity of steel, because V has the effect of crystal grain thinning, raising intensity that not only can steel can also improve the toughness of steel.In addition, reduced the content of S, P impurity element, helped improving the clarity of steel, reduced in length and breadth to performance difference.The mechanical property of stainless steel of the present invention and existing steel grade is relatively seen table 3 (1040 ℃+480 ℃ timeliness of sample warp 1 hour).
The mechanical property of table 3 stainless steel of the present invention and existing steel grade relatively
2, stainless steel of the present invention adopts electric furnace+external refining (AOD)+vacuum consumable technology to smelt, and gas content is low, and hydrogen reaches 0.0001PPm, oxygen reaches 0.005PPm.Existing steel grade adopts electric furnace+external refining (AOD)+electroslag process to smelt, and hydrogen is generally at 0.0004PPm～0.0006PPm, oxygen 0.02PPm～0.05PPm.The gas content height will make steel inclusion increase, and reduce the toughness index of steel, and in addition, electroslag smelting is under atmosphere, to smelt, and Nb is easy to oxidization burning loss, but the present invention adopts vacuum consumable technology to smelt, and has just avoided Nb element problem of oxidation.
3, steel grade of the present invention has been produced Φ 400～Φ 600mm great circle and has been forged rod; And obtained the good combination of HS and plasticity; Tensile strength reaches 1390Mpa, and ys reaches 1300Mpa, and elongation reaches 15%; Reduction of area reaches 48% (lateral performance), can satisfy the requirement of high-strength parts such as high pressure valve, oil drilling, efficient heavy-duty machinery to material property.And existing steel grade can only be produced Φ 300mm and forges rod, and the plasticity index elongation only reaches 11%, and reduction of area reaches 40%.
Description of drawings
Fig. 1 is δ-ferritic metallographic structure photo of existing steel grade 0Cr17Ni4Cu4Nb.
Fig. 2 is the δ-ferritic metallographic structure photo of the martensitic precipitation of the embodiment of the invention 5.
Embodiment
Below combine accompanying drawing that the present invention is made more detailed description with embodiment.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
Embodiment 1
Pressing the chemical ingredients electric furnace shown in the table 3+external refining smelts; In prereduction slag charge and reduction slag charge, add Al ingot or Ti-Te alloy, terminal point C is controlled at 0.02wt% after the oxygen blast, and before the tapping of AOD stove, adds the Nb-Te alloy; Cast Φ 510mm electrode is through consumable remelting Φ 610mm consumable ingot.Steel ingot shove charge annealing after the smelting, 820～860 ℃ of annealing temperatures, soaking time >=10h, stove are as cold as 500 ℃ of air coolings of coming out of the stove.Steel ingot after the annealing advances the process furnace heating, prior to 500 ℃ of preheating 2.5h, is warmed up to 800 ℃ by 50 ℃/h again, and insulation 2h is warmed up to 1200 ℃ by 80 ℃/h subsequently again, insulation 3.5 ± 0.5h.Forge then, opening and forging temperature is 1150 ℃, 990 ℃ of finishing temperatures.Forge the back air cooling again through 650 ℃ of annealing, soaking time >=48h is cooled to 550 ℃ of air coolings of coming out of the stove by 20 ℃/h.
Embodiment 2
Steel ingot after the annealing is warmed up to 820 ℃ by 45 ℃/h again in 520 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1190 ℃ by 70 ℃/h subsequently again, insulation 3h.Forge then, opening and forging temperature is 1140 ℃, and 1020 ℃ of finishing temperatures are forged the back air cooling again through 620～680 ℃ of annealing.All the other embodiments are with embodiment 1.
Embodiment 3
Steel ingot after the annealing is warmed up to 840 ℃ by 50 ℃/h again in 550 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1195 ℃ by 75 ℃/h subsequently again, insulation 3.7h.Forge then, opening and forging temperature is 1130 ℃, and 980 ℃ of finishing temperatures are forged the back air cooling again through 620～680 ℃ of annealing.All the other embodiments are with embodiment 1.
Embodiment 4
Steel ingot after the annealing is warmed up to 850 ℃ by 40 ℃/h again in 560 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1205 ℃ by 80 ℃/h subsequently again, insulation 4h.Forge then, opening and forging temperature is 1100 ℃, and 880 ℃ of finishing temperatures are forged the back air cooling again through 620～680 ℃ of annealing.All the other embodiments are with embodiment 1.
Embodiment 5
Cast Φ 760mm electrode is through consumable remelting Φ 810mm consumable ingot.Steel ingot after the annealing is warmed up to 810 ℃ by 45 ℃/h again in 580 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1190 ℃ by 75 ℃/h subsequently again, insulation 4.5h.Forge then, opening and forging temperature is 1135 ℃, and 890 ℃ of finishing temperatures are forged the back air cooling again through 620～680 ℃ of annealing.All the other embodiments are with embodiment 1.
Embodiment 6
Cast Φ 760mm electrode is through consumable remelting Φ 810mm consumable ingot.Steel ingot after the annealing is warmed up to 830 ℃ by 40 ℃/h again in 600 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1200 ℃ by 80 ℃/h subsequently again, insulation 5h.Forge then, opening and forging temperature is 1170 ℃, and 1000 ℃ of finishing temperatures are forged the back air cooling again through 620～680 ℃ of annealing.All the other embodiments are with embodiment 1.
The chemical ingredients (wt%) of table 4 embodiment of the invention 1-6 martensitic precipitation
| Embodiment | C | Si | Mn | S | P | Ni | Cr | Cu | V | Nb+Ta | N |
| 1 | 0.03 | 0.65 | 0.45 | 0.002 | 0.020 | 4.70 | 14.50 | 2.74 | 0.05 | 0.38 | 0.018 |
| 2 | 0.04 | 0.69 | 0.49 | 0.002 | 0.020 | 4.85 | 14.98 | 3.31 | 0.08 | 0.36 | 0.020 |
| 3 | 0.03 | 0.69 | 0.51 | 0.002 | 0.018 | 4.86 | 15.04 | 3.33 | 0.07 | 0.36 | 0.025 |
| 4 | 0.05 | 0.62 | 0.50 | 0.002 | 0.020 | 4.86 | 14.91 | 3.57 | 0.07 | 0.37 | 0.015 |
| 5 | 0.04 | 0.72 | 0.44 | 0.002 | 0.019 | 4.28 | 14.74 | 3.06 | 0.05 | 0.22 | 0.022 |
| 6 | 0.05 | 0.45 | 0.50 | 0.003 | 0.020 | 4.21 | 14.95 | 3.23 | 0.06 | 0.25 | 0.030 |
Test Example 1
The martensitic precipitation of embodiment of the invention 1-6 after 1040 ℃ of solid solution+480 ℃ timeliness were handled in 1 hour, is carried out performance test, table with test results 5.
The The performance test results of the martensitic precipitation of table 5 embodiment of the invention 1-6
Test Example 2
Martensitic precipitation to the existing steel grade 0Cr17Ni4Cu4Nb and the embodiment of the invention 5 carries out microtexture research, and its metallographic structure photo is seen Fig. 1 and Fig. 2 respectively.It seems that from Fig. 1 δ-ferrite content is many, and the δ-ferrite content among Fig. 2 is obviously less, can't see basically.
Claims (4)
1. the method for manufacture of a martensite precipitation hardening stainless steel for structural member comprises smelting, annealing, heating, forging, annealing operation again, it is characterized in that electric furnace, AOD refining and vacuum consumable technology are adopted in said smelting;
In said vacuum consumable technology, speed of melting is 6～8kg/min,, electrode weight begins to bind when remaining 200～300kg, and be 50～100kg to smelting end electrode residuals weight;
In said heating process, steel ingot is warmed up to 800～850 ℃ by 40～50 ℃/h again in 500～600 ℃ of preheating 2.5h, and insulation 2h is warmed up to 1200 ± 10 ℃ by 70～80 ℃/h subsequently again, insulation 3.5～5h;
In said annealing process again, 620～680 ℃ of annealing temperatures, soaking time >=48h is cooled to 550 ℃ of air coolings of coming out of the stove by 20 ℃/h;
The chemical ingredients of said martensitic precipitation comprises: C≤0.05wt%, Cr:13.50～15.50wt%, Cu:2.5～4.0wt%, Ni:3.0～5.0wt%, Nb+Ta:0.15～0.40wt%, N:0.010～0.040wt%, V:0.050～0.15wt%, Si≤0.80wt%, Mn≤1.00wt%, P≤0.025wt%, S≤0.010wt%, and surplus is Fe and unavoidable impurities;
The elongation of said martensite precipitation hardening stainless steel for structural member reaches 15%, and reduction of area reaches 48%.
2. method of manufacture according to claim 1; It is characterized in that, in said AOD refining process, in prereduction slag charge and reduction slag charge, add Al ingot or Ti-Te alloy; Terminal point C is controlled at 0.02wt% after the oxygen blast, and before the tapping of AOD stove, adds the Nb-Te alloy.
3. method of manufacture according to claim 1 is characterized in that, the steel ingot shove charge annealing after the smelting, and 820～860 ℃ of annealing temperatures, soaking time >=10h, stove are as cold as 500 ℃ of air coolings of coming out of the stove.
4. method of manufacture according to claim 1 is characterized in that, it is 1100～1170 ℃ that the opening of said forging process forged temperature, finishing temperature >=850 ℃.
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