CN101372734A - Martensite stainless steel and manufacturing method thereof - Google Patents
Martensite stainless steel and manufacturing method thereof Download PDFInfo
- Publication number
- CN101372734A CN101372734A CNA2007100452206A CN200710045220A CN101372734A CN 101372734 A CN101372734 A CN 101372734A CN A2007100452206 A CNA2007100452206 A CN A2007100452206A CN 200710045220 A CN200710045220 A CN 200710045220A CN 101372734 A CN101372734 A CN 101372734A
- Authority
- CN
- China
- Prior art keywords
- steel
- stainless steel
- percent
- equal
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Abstract
The invention discloses a martensitic stainless steel and a manufacture method thereof. The martensitic stainless steel is characterized in that the stainless steel comprises the following chemical elements by weight percentage: 0.13 to 0.18 percent of C, 0.06 to (C-0.06) percent of N, less than or equal to 1.00 percent of Si, less than or equal to 1.00 percent of Mn, 12.00 to 14.00 percent of Cr, less than or equal to 0.035 percent of P, less than or equal to 0.030 percent of S, and the residual amount of Fe and inevitable impurities, wherein, C plus N is more than or equal to 0.21 percent. The manufacture method comprises the following steps: 1) continuous casting or mold casting is carried out, and then cooling is carried out at less than or equal to 10 DEG C/minute; 2) hot rolling is carried out with heating temperature of 1,200 to 1,250 DEG C, initial rolling temperature of less than or equal to 1,180 DEG C, and finishing temperature of more than or equal to 980 DEG C, and a steel coil is naturally cooled after rolling; 3) conventional annealing is carried out at the temperature of 780 to 900 DEG C; 4) conventional normalizing is carried out at the temperature of 1,000 to 1,150 DEG C. The martensitic stainless steel and the method can improve the hardness and the corrosion resistance of the martensitic stainless steel, and can reduce the manufacturing cost at the same time.
Description
Technical field
The present invention relates to the ferrous metallurgy field, belong to Martensite Stainless Steel especially.
Background technology
Often adopt Cr13 type Martensite Stainless Steel when producing scissors, table knife, five metals cutter, this class stainless steel has higher intensity, hardness, and has certain solidity to corrosion.
In order to guarantee that Martensite Stainless Steel has higher hardness and certain solidity to corrosion, the 2Cr13 steel has 0.16-0.25%C (typical 2Cr13 steel 0.22%C), the basic chemical ingredients of 12-14%Cr.Because C content is higher in the steel, steel segregation in process of production is more serious, and solidity to corrosion is relatively poor relatively.For guaranteeing that steel has good corrosion resistance, except the The addition of C r that in steel, adds, also in steel, add Ni, also add Mo, Cu sometimes, have high rigidity to guarantee steel, table 1 is the relevant patent of Cr13 type Martensite Stainless Steel.
Chemical ingredients comparison/the wt% of table 1 Cr13 type Martensite Stainless Steel patent
| Patent publication No. | C | Si | Mn | Cr | Mo | Ni | N | P | S | Other |
| CN11 4564 4 | 0.15～0.4 0 | ≤2.00 | ≤2.00 | 11.00～15 .00 | 1.00～3.0 0 | 0.10～1 .50 | 0.02～0.1 5 | - | - | Cu： 0.12～ 2.0 |
| CN12 8718 4 | 0.27～0.3 5 | ≤1.00 | ≤1.00 | 12.00～14 .00 | 0.40～1.0 0 | 3.00～5 .00 | - | ≤0.04 | ≤0.04 | - |
| JP100 18002 | 0.15～0.4 0 | ≤2.00 | ≤2.00 | 11.00～15 .00 | 1.00～3.0 0 | 0.20～2 .00 | 0.01～0.1 5 | - | - | Cu： 0.12～ 4.0 |
| EP173 9199 | 0.40～0.5 5 | 0.8～1.5 | 0.70～0.8 5 | 13.00～14 .00 | 1.00～1.5 0 | 0.20～0 .40 | 0.02～0.0 4 | - | - | - |
| CN16 2418 2 | 0.12～0.1 7 | ≤1.00 | ≤2.00 | 12.50～14 .50 | - | - | 0.06～0.1 0 | ≤0.04 | ≤0.04 | O：≤ 0.01 0.210 ≤ C+N ≤ 0.265 |
| 2Cr13 | 0.16～0.2 5 | ≤1.00 | ≤1.00 | 12.00～14 .00 | - | - | - | ≤ 0.035 | ≤0.03 | - |
The purpose that adds C is to obtain stable high temperature austenite phase, increases the hardening capacity of steel, can obtain martensitic stucture under the air cooling condition.But higher C is unfavorable for the solidity to corrosion that improves steel, so people add the C that a certain amount of austenite former N, Ni come instead of part sometimes, as CN1145644, CN1287184, JP10018002, CN11624182.Add Mo, Cu in the steel, can improve the solidity to corrosion of steel, improve the intensity and the hardness of steel, increase the secondary hardening effect, Mo can also improve the hot strength and the temper resistance of steel, as CN1145644, JP10018002, EP1739199.But behind the alloying elements such as adding Ni, Mo, Cu, the cost of steel significantly rises.The adding of N is preferred for improving stainless steel hardness and solidity to corrosion, yet, the solid solubility of N in the high temperature ferrite is very low, will in the transition process of steel L → δ, separate out during the too high levels of N, in steel, stay pore, thereby in the alloying process of N, the N content of how controlling in the steel is a key point.
The content of regulation C is 0.12～0.17% among the CN11624182, and N content is 0.06～0.10%.In fact, the solid solubility of N in the high temperature ferrite and the content of other alloying elements, particularly C content has very big relation.Facts have proved, when C content is 0.13, will in strand, form pore when N content is 0.095% left and right sides; When carbon content was 0.18%, it is still not obvious that the content of N reaches in 0.11% o'clock steel pore.
Summary of the invention
The objective of the invention is by a kind of Martensite Stainless Steel and manufacture method thereof are provided, make the Martensite Stainless Steel of producing possess higher hardness and better corrosion resisting property, when reducing production costs, can satisfy better and make of the requirement of table knife tool Martensite Stainless Steel.
Technical scheme of the present invention is: a kind of Martensite Stainless Steel, the chemical element that comprises following weight percent proportioning: C:0.13～0.18%, N:0.06～(C-0.06) %, and C+N 〉=0.21%, Si≤1.00%, Mn≤1.00%, Cr:12.00～14.00%, P≤0.035%, S≤0.030%, all the other are Fe and unavoidable impurities.
Preferably, the weight percent proportioning of described Cr element is: 13.00～14.00%.
C: the hardenability and the intensity that improve steel.Crossing low carbon can cause the hardness of steel not reach service requirements; Too high carbon can increase the segregation of steel in casting process, also can reduce the corrosion resistance nature of steel simultaneously.The zone of reasonableness of C content may be prescribed as 0.13～0.18%, simultaneously rational coupling must be arranged with the content of N.
N: improve the hardenability and the intensity of steel, postpone separating out of carbide.Effect is not obvious when the content of nitrogen in Martensite Stainless Steel is lower than 0.06%.The content of N in Martensite Stainless Steel is limited by the solid solubility of N in ferrite mainly, and solid solubility and C content (0.13～0.18% scope in) relation that have (C-0.06) % of N in ferrite, therefore, the content of N may be prescribed as 0.06～(C-0.06) %.
In the 2Cr13 steel, carbide to separate out temperature higher, it is bigger to separate out tendency, reduces the temperature of separating out that C content can reduce carbide, also favourable to the solidity to corrosion that improves steel; N is strong austenizer, is again the important element that improves the corrosion-resistant ability of steel, adds hardness, solidity to corrosion that N can improve steel; The C content of N in ferritic solid solubility of high temperature and steel has very big relation, therefore should be noted that when in steel, adding N with steel in the C amount be complementary, low excessively N amount can make the hardenability of steel not enough, the N too high levels can cause steel to produce pore.
C+N: the amount of C+N mainly is in order to guarantee that steel has hardenability preferably in the control steel, makes the hardness of steel reach the requirement of HRC 〉=48.
Si: a kind of impurity element that exists in the steel.When Si content is low, the mechanical property of steel there is not big influence, toughness deterioration when Si content surpasses 1.00%.
Mn: can improve the hardening capacity of steel to a certain extent, increase the intensity of steel; With the fixing S in the steel of the form of MnS, and surpass 1.00% o'clock toughness deterioration.
Cr: the corrosion resistance nature that improves steel.When reaching 12.00%, improves Cr content the anti-pitting attack and the crevice corrosion of steel.Excessively add Cr and can increase production cost.Therefore, the zone of reasonableness 12.00～14.00% of Cr content is for the solidity to corrosion that improves steel can be more preferably 13.00～14.00%.
P: the impurity element in the steel.Consider that the low P amount of too much requirement can increase production cost, its upper limit may be prescribed as≤and 0.035%.
S: the impurity element in the steel, worsen solidity to corrosion, content is few more good more.Consider that the low S amount of too much requirement can increase production cost, its upper limit may be prescribed as≤and 0.030%.
A kind of manufacture method of Martensite Stainless Steel may further comprise the steps:
(1) continuous casting or die casting; Will guarantee when continuous casting or die casting that all even surface quality of strand internal component is good, the steel ingot of die casting need be rolled into steel billet.Continuously cast bloom and steel billet need to adopt the cooling of≤10 ℃/min speed of cooling, and this is for fear of the too fast cracking that causes of martensitic transformation.
(2) hot rolling: with blank heating to 1200 ℃～1250 ℃, be incubated to blank temperature even, start rolling temperature≤1180 ℃, back coil of strip naturally cooling is rolled in finishing temperature 〉=980 ℃, will avoid Quench modes such as wind, water pouring to cool off during high temperature.Continuously cast bloom or the bloom Heating temperature before hot rolling is 1200 ℃～1250 ℃, on the one hand carbide is dissolved fully, can obtain uniform austenitizing tissue on the other hand; Can guarantee that steel has good rolling performance when start rolling temperature≤1180 ℃, finishing temperature 〉=980 ℃; Avoid wind, water to drench during coil of strip high temperature, to avoid the too fast cracking that causes of martensitic transformation.
(3) conventional annealing: 780 ℃～900 ℃ of annealing temperatures; Coils of hot-rolled steel is organized as evenly tiny ferrite matrix and globular carbide after 780 ℃～900 ℃ annealing, guarantee that steel have good processing properties so on the one hand, also gets ready for normalizing treatment on the other hand.
(4) conventional normalizing: 1000 ℃～1150 ℃ of normalizing temperatures.The normalizing Heating temperature is 1000 ℃～1150 ℃ can make carbide fully dissolve, and obtains uniform austenite structure, is martensitic stucture after the normalizing.
The present invention compared with prior art has following beneficial effect:
1. the design about the weight percent proportioning of chemical element can make Martensite Stainless Steel segregation of carbide in castingprocesses less among the present invention, avoids pore to produce simultaneously.
2. the Martensite Stainless Steel produced of the present invention possesses higher hardness, solidity to corrosion preferably, is more suitable for making cutter etc. and bears heavily stressed and need certain corrosion proof utensil or part.
3. the present invention has improved quality product, has reduced production cost.
Description of drawings
Fig. 1 is the metallograph of steel after the hot rolling of embodiment 1.
Fig. 2 is the metallograph of steel after the hot rolling of Comparative Examples 1.
Fig. 3 is the metallograph of the tissue of steel after the normalizing of embodiment 1.
Fig. 4 is the metallograph of the tissue of steel after the normalizing of Comparative Examples 1.
Fig. 5 is that the pitting potential of 4 embodiment and Comparative Examples 1 is measured synoptic diagram.
Fig. 6 is the synoptic diagram of C content to the influence of N in ferrite.
Fig. 7 is the test steel ingot figure of embodiment 3.
Fig. 8 is the test steel ingot figure of Comparative Examples 3.
Embodiment
Obtain composition Martensite Stainless Steel ingot as described in Table 1 through smelting, just roll into the thick steel billet of 30mm, steel billet is cooled to below 250 ℃ with the speed of≤10 ℃/min; Steel billet is heated to 1230 ℃, is incubated to temperature and carries out hot rolling after evenly; 1180 ℃ of start rolling temperatures, 1000 ℃ of finishing temperatures, hot rolling obtains the sheet material that thickness is 8mm.The hot-rolled sheet material is standby after 820 ℃ of annealing, and it is standby that the part material carries out normalizing treatment.
The chemical ingredients of table 1 steel of the present invention and compared steel
HRC hardness value after the thermal treatment of table 2 test steel
In the table 1, the steel grade of the present invention of experimental example 1～4, its composition is in the composition range of regulation, and Comparative Examples 1～3 is a compared steel, wherein Comparative Examples 1 is typical 2Cr13 Martensite Stainless Steel.Can know that with reference to table 1 embodiment 1 steel is compared with Comparative Examples 1 steel, C content is lower, and N content is higher, and C+N is more or less the same.
Table 2 is the Rockwell hardness number after each embodiment and Comparative Examples 1, Comparative Examples 2 normalizings.When material is used as cutter, general requirement HRC value 〉=48, preferably HRC value 〉=50.Associative list 1, table 2 can know, when the C+N in the steel 〉=0.21%, steel carries out normalizing in 1000 ℃～1150 ℃ temperature range, hardness all reaches HRC value 〉=48, major part reaches the requirement of HRC value 〉=50, compares with Comparative Examples 1 (typical 2Cr13 steel), and hardness is significantly improved.Comparatively speaking, the hardness value of embodiment 1 is on the low side, this with steel in the value of C+N low relevant.When C+N≤0.21%, be difficult to guarantee that the hardness after the steel normalizing reaches HRC value 〉=48, be 0.198 as C+N in Comparative Examples 2 steel, its HRC value does not have to reach 48 requirement.Therefore, when the composition of design steel, should be noted that to guarantee C+N 〉=0.21% in the steel.
It can also be seen that by table 2 hardness of embodiment steel when 950 ℃ of normalizings is on the low side, this therewith under the temperature steel austenitizing not exclusively relevant.When normalizing temperature reaches 1100 ℃, rising along with normalizing temperature, the hardness of material begins to be downward trend, can see by the trend that changes, when surpassing 1150 ℃, the normalizing temperature of material is difficult to guarantee that the HRC value of material reaches 48, this is owing to when high temperature normalizing cools down, have more austenite in the steel, and the hardenability of steel is descended.This shows that the normalizing treatment temperature range of steel of the present invention is 1000～1150 ℃.
Can be seen by Fig. 1 and Fig. 2, after hot rolling, as shown in Figure 2, have tangible ferrite banding tissue and granular carbide in the steel of table 1 Comparative Examples 1, this uneven being organized in is difficult in the long-term heat-processed eliminate up hill and dale.By contrast, organize more evenly after the hot rolling of Fig. 1 for the steel of table 1 embodiment 1, separating out of carbide is tiny and even, and this tissue is quite favourable for material hot treatment.
Fig. 3 and Fig. 4 are table 1 embodiment 1 and the metallograph of Comparative Examples 1 after 1050 ℃ of normalizings, can see by Fig. 4, can see in the tissue after the 1 steel normalizing of table 1 Comparative Examples that tangible carbide separates out, in table 1 embodiment 1, then can't see the phenomenon of separating out of tangible carbide.As seen, steel of the present invention separating out in the normalizing process is inclined to less.
Fig. 5 is each embodiment of table 1 and the pitting potential of Comparative Examples 1 steel through recording in 3.5%NaCl (20 ℃) aqueous solution after 1050 ℃ of normalizings, and pitting potential is a major criterion of weighing the pitting corrosion resistance of steel, and pitting potential is high more, and the pitting resistance of steel is good more.As seen from Figure 5, the pitting potential of steel grade of the present invention all is higher than traditional 2Cr13 Martensite Stainless Steel (seeing Table 1 Comparative Examples 1).Associative list 1 can find that under the essentially identical situation of other compositions, along with the increase of C content in the steel of the present invention, the pitting potential of steel is downward trend.When C content reached 0.18, the solidity to corrosion of the solidity to corrosion of steel and 2Cr13 steel was close, if the continuation of C content increases, its solidity to corrosion can further reduce, and therefore, has corrosion-resistant ability preferably in order to make steel of the present invention, and C content answers≤0.18% in the steel.
Fig. 6 be in the 0.08N-0.53Mn-0.46Si-13.7Cr steel that calculates with Thermercalc C to the influence of N in ferrite.As seen from Figure 6, the steel of this composition the process of setting of L → high temperature delta ferrite at first takes place, and the solubleness of N in the high temperature delta ferrite is less from liquid cooled following time, and different along with the variation of composition.Being it can also be seen that by Fig. 6, is the steel of 0.08N-0.53Mn-0.46Si-13.7Cr for composition, and steel is from the high temperature cooling zone that Shi Douhui separates out mutually through gas of getting off when C＜0.15%, and along with the increase of carbon content, the tendency of separating out of gas descends.By the calculating among Fig. 6 as can be known, when C 〉=0.15%, containing the N amount and can reach 0.08% in the steel.In actual smelting process because the effect of molten steel surface tension force, pressure own, C content be 0.14% o'clock can be so that do not produce tangible bubble in the steel.In conjunction with more detailed calphad and top analysis, can draw, 0.13≤C≤0.18% o'clock, the solid solubility of N is about (C-0.06) %.Carbon content in table 1 embodiment 3 and the Comparative Examples 3 is respectively 0.179% and 0.142%, and the N solid solubility that can obtain them according to above calculating formula is respectively 0.119% and 0.082%, and the N that adds in the smelting process of reality is respectively 0.112%, 0.095%.The result finds no pore on the ingot casting of table 1 embodiment 3, and has found a large amount of pores on the ingot casting of Comparative Examples 3 by Fig. 7 and Fig. 8 as can be seen.
Claims (4)
1. Martensite Stainless Steel, it is characterized in that comprising the chemical element of following weight percent proportioning: C:0.13～0.18%, N:0.06～(C-0.06) %, and C+N 〉=0.21%, Si≤1.00%, Mn≤1.00%, Cr:12.00～14.00%, P≤0.035%, S≤0.030%, all the other are Fe and unavoidable impurities.
2. Martensite Stainless Steel as claimed in claim 1, its feature also is: the weight percent proportioning of described Cr element is: 13.00～14.00%.
3. the manufacture method of a Martensite Stainless Steel is characterized in that may further comprise the steps:
(1) continuous casting or die casting, slow cooling;
(2) hot rolling: before the hot rolling through 1200 ℃～1250 ℃ heating, start rolling temperature≤1180 ℃, finishing temperature 〉=980 ℃, the coil of strip naturally cooling after rolling;
(3) conventional annealing: 780 ℃～900 ℃ of annealing temperatures;
(4) conventional normalizing: 1000 ℃～1150 ℃ of normalizing temperatures.
4. the manufacture method of Martensite Stainless Steel as claimed in claim 3 is characterized in that in the described step (1), continuously cast bloom or cogged ingot speed of cooling≤10 ℃/min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2007100452206A CN101372734A (en) | 2007-08-24 | 2007-08-24 | Martensite stainless steel and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2007100452206A CN101372734A (en) | 2007-08-24 | 2007-08-24 | Martensite stainless steel and manufacturing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101372734A true CN101372734A (en) | 2009-02-25 |
Family
ID=40447107
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNA2007100452206A Pending CN101372734A (en) | 2007-08-24 | 2007-08-24 | Martensite stainless steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101372734A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102353759A (en) * | 2011-09-30 | 2012-02-15 | 山东泰山钢铁集团有限公司 | Detection technology of microscopic bubbles in stainless steel production process |
| CN102363864A (en) * | 2011-10-10 | 2012-02-29 | 刘群联 | Method for manufacturing martensite stainless steel tubes |
| CN102605258A (en) * | 2011-01-25 | 2012-07-25 | 宝山钢铁股份有限公司 | Martensitic stainless steel and manufacturing method thereof |
| CN102676941A (en) * | 2012-04-25 | 2012-09-19 | 李小强 | Tungsten carbide particle-reinforced wear-resistant corrosion-resistant stainless steel and preparation method thereof |
| CN104471095A (en) * | 2012-07-16 | 2015-03-25 | Posco公司 | Martensitic stainless steel and method for manufacturing same |
| CN110923415A (en) * | 2019-12-05 | 2020-03-27 | 浙江艾奥巴美新材料有限公司 | Nickel-free martensitic stainless steel and manufacturing process thereof |
| CN112008498A (en) * | 2019-05-28 | 2020-12-01 | 宝山钢铁股份有限公司 | Method for eliminating surface defects of medium-high carbon martensitic stainless steel continuous casting blank |
| WO2021187706A1 (en) * | 2020-03-20 | 2021-09-23 | 주식회사 포스코 | Highly anticorrosive martensitic stainless steel, and manufacturing method therefor |
| CN114606370A (en) * | 2022-02-20 | 2022-06-10 | 山西太钢不锈钢股份有限公司 | Method for reducing shear delamination defect of nitrogen-containing martensitic stainless steel hot-rolled steel plate |
-
2007
- 2007-08-24 CN CNA2007100452206A patent/CN101372734A/en active Pending
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102605258A (en) * | 2011-01-25 | 2012-07-25 | 宝山钢铁股份有限公司 | Martensitic stainless steel and manufacturing method thereof |
| CN102605258B (en) * | 2011-01-25 | 2014-05-07 | 宝山钢铁股份有限公司 | Martensitic stainless steel and manufacturing method thereof |
| CN102353759B (en) * | 2011-09-30 | 2015-10-21 | 山东泰山钢铁集团有限公司 | The characterization processes of micro-bubble in producing stainless steel process |
| CN102353759A (en) * | 2011-09-30 | 2012-02-15 | 山东泰山钢铁集团有限公司 | Detection technology of microscopic bubbles in stainless steel production process |
| CN102363864A (en) * | 2011-10-10 | 2012-02-29 | 刘群联 | Method for manufacturing martensite stainless steel tubes |
| CN102676941A (en) * | 2012-04-25 | 2012-09-19 | 李小强 | Tungsten carbide particle-reinforced wear-resistant corrosion-resistant stainless steel and preparation method thereof |
| CN104471095A (en) * | 2012-07-16 | 2015-03-25 | Posco公司 | Martensitic stainless steel and method for manufacturing same |
| CN104471095B (en) * | 2012-07-16 | 2016-11-02 | Posco公司 | Martensitic stainless steel and manufacture method thereof |
| CN112008498A (en) * | 2019-05-28 | 2020-12-01 | 宝山钢铁股份有限公司 | Method for eliminating surface defects of medium-high carbon martensitic stainless steel continuous casting blank |
| CN112008498B (en) * | 2019-05-28 | 2021-11-16 | 宝山钢铁股份有限公司 | Method for eliminating surface defects of medium-high carbon martensitic stainless steel continuous casting blank |
| CN110923415A (en) * | 2019-12-05 | 2020-03-27 | 浙江艾奥巴美新材料有限公司 | Nickel-free martensitic stainless steel and manufacturing process thereof |
| CN110923415B (en) * | 2019-12-05 | 2021-12-07 | 浙江艾奥巴美新材料有限公司 | Medical nickel-free martensitic stainless steel and manufacturing process thereof |
| WO2021187706A1 (en) * | 2020-03-20 | 2021-09-23 | 주식회사 포스코 | Highly anticorrosive martensitic stainless steel, and manufacturing method therefor |
| CN115667569A (en) * | 2020-03-20 | 2023-01-31 | 株式会社Posco | Highly corrosion-resistant martensitic stainless steel and method for producing same |
| CN114606370A (en) * | 2022-02-20 | 2022-06-10 | 山西太钢不锈钢股份有限公司 | Method for reducing shear delamination defect of nitrogen-containing martensitic stainless steel hot-rolled steel plate |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107779577B (en) | A kind of garden tool set steel that processing performance is excellent and its production method | |
| EP4130316A1 (en) | Pre-hardened mirror mold steel plate and manufacturing method therefor | |
| CN101372734A (en) | Martensite stainless steel and manufacturing method thereof | |
| CN103882314B (en) | A kind of 42CrMo steel cold-reduced sheet and production method thereof | |
| CN103710638B (en) | A kind of Martensite Stainless Steel and manufacture method thereof | |
| CN109735777B (en) | Anti-oxidation hot-work die steel and preparation method thereof | |
| CN105063492A (en) | Hot-rolled steel for car friction plate and preparation method of hot-rolled steel | |
| CN111378900B (en) | Steel for wear-resistant and corrosion-resistant chain plate and manufacturing method thereof | |
| CN102191438A (en) | Steel plate for seamless high pressure gas cylinder, and manufacture method thereof | |
| CN114107792A (en) | 780 MPa-grade high-surface ultrahigh-hole-expansion steel and manufacturing method thereof | |
| CN106086683A (en) | By tensile strength >=1700MPa thin hot forming steel and the production method of sheet billet Direct Rolling | |
| CN111411311A (en) | Steel for die casting corrosion-resistant chain plate and manufacturing method thereof | |
| CN111575578B (en) | Hot-rolled chain plate steel strip with excellent wear resistance and manufacturing method thereof | |
| CN111549274A (en) | Wear-resistant Nb-containing chain plate hot-rolled steel strip and manufacturing method thereof | |
| JP2010514928A (en) | Ferritic stainless steel with excellent corrosion resistance and stretch formability and method for producing the same | |
| CN112430771B (en) | Cold-rolled steel plate for precision stamping high-speed cutting chain saw blade and manufacturing method thereof | |
| CN105002434A (en) | Hot-rolled steel for steel disc of vehicle driven plate and preparation method of hot-rolled steel | |
| CN113088813A (en) | Steel for hot-rolled saw blade and production method thereof | |
| CN101476086A (en) | Economic steel for plastic cavity die and manufacturing method thereof | |
| CN105296866B (en) | A kind of blade steel, production method and blade processing method | |
| CN101693982B (en) | Martensite corrosion-resisting steel plate for cutting tool and manufacture method thereof | |
| CN101638750A (en) | Martensitic stainless steel for cutting tool and manufacturing method thereof | |
| CN100593580C (en) | Nickel-saving high-strength stainless hot-rolling belt steel and preparation method thereof | |
| CN110079733B (en) | Ultra-thin ultra-high strength medium carbon bainite steel and manufacturing method thereof | |
| CN107988549A (en) | A kind of low yield strength ratio cylinder steel and its manufacture method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Open date: 20090225 |