WO2021044889A1 - マルテンサイト系ステンレス鋼板およびマルテンサイト系ステンレス鋼部材 - Google Patents
マルテンサイト系ステンレス鋼板およびマルテンサイト系ステンレス鋼部材 Download PDFInfo
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a martensitic stainless steel sheet and a martensitic stainless steel member having excellent corrosion resistance after quenching. More specifically, the present invention relates to martensitic stainless steel having excellent corrosion resistance even when air-cooled and hardened, which is used for manufacturing Western tableware knives, looms, tools, disc brakes and the like.
- Martensitic stainless steel sheets such as SUS420J1 and SUS420J2 steel are generally used for tools such as Western tableware knives (table knives), scissors, weaving machines, and calipers. In such applications, it is difficult to use plating, painting, and rust preventive oil, and the material itself is required to have rust resistance. It is also important that it does not wear easily, and high hardness is required.
- the manufacturing process of Western tableware knives, etc. is usually made by die-cutting from a steel plate, heating, quenching, and then polishing to make a knife.
- the quenching process is often performed by air cooling, which also depends on the characteristics of the martensitic stainless steel sheet, which has excellent quenching properties.
- Patent Document 1 discloses a martensitic stainless steel that is air-cooled and has excellent corrosion resistance during quenching.
- N is added up to about 0.06% as an element for improving corrosion resistance.
- Patent Document 2 discloses a steel to which N is further added.
- Patent Document 3 discloses a steel in which N is further increased by using special equipment.
- the present inventors first investigated the rusting condition of the table knife in detail. As a result, it was clarified that the rusting site starts from the end face of the steel sheet, more specifically, the central part of the thickness of the steel sheet. Furthermore, the formation of a ⁇ ferrite phase ( ⁇ Fe phase) due to macrosegregation was confirmed, and the grain boundaries of this ⁇ Fe became the accumulation sites of carbides, and the carbides melted by heating during quenching, and then grain boundaries during cooling. It was found that the mechanism of quenching is that precipitation occurs, resulting in sensitization and intergranular corrosion. It was also found that the rusting depends on the cooling rate during quenching.
- the cooling rate varies greatly depending on the quenching equipment, but when evaluated by the average cooling rate from the quenching temperature to 600 ° C, which is the temperature at which carbide precipitation is almost completed, the cooling rate exceeds 100 ° C / s in water quenching.
- the cooling rate is only about 5 ° C / s, and carbide precipitation cannot be suppressed and quenching is unlikely to occur. It turns out that is likely to occur.
- a martensitic stainless steel sheet having a ⁇ p of 120 or more represented by the following formula (1) When the martensitic stainless steel sheet is held at 1050 ° C. for 30 minutes, then air-cooled and quenched, and tempered at 150 ° C. for 30 minutes, the area of ⁇ ferrite ( ⁇ Fe) present in the center of the plate thickness in the plate thickness cross section.
- ⁇ p 420C + 470N + 30Ni + 7Mn + 9Cu-11.5Cr-11.5Si-12Mo-23V-47Nb-52Al + 189 ... Equation (1)
- the element symbol in the formula (1) means the content (mass%) of the element.
- the ⁇ p represented by the following formula (1) is 120 or more, and Further, a martensitic stainless steel member characterized in that the area ratio of ⁇ ferrite ( ⁇ Fe) existing in the central portion of the plate thickness in the plate thickness cross section is 0.1 to 1%.
- ⁇ p 420C + 470N + 30Ni + 7Mn + 9Cu-11.5Cr-11.5Si-12Mo-23V-47Nb-52Al + 189 ... Equation (1)
- the element symbol in the formula (1) means the content (mass%) of the element.
- the martensitic stainless steel sheet of the present invention has excellent corrosion resistance, especially end face corrosion resistance, while maintaining sufficient hardness to withstand use for martensitic stainless steel applications such as table knives and other Western tableware. Therefore, when it is used as a martensitic stainless steel member such as a Western tableware knife, it can be expected to have an effect of improving corrosion resistance and prolonging the product life.
- C is an element that determines the quenching hardness together with N, and is required to be 0.100% or more in order to obtain the hardness required for a Western tableware knife. It is preferably 0.110% or more, and 0.120% or more.
- the quenching hardness becomes larger than necessary, the load during polishing increases, and the toughness also decreases.
- Cr carbides are likely to precipitate during air-cooling quenching and the corrosion resistance is likely to be impaired, so the content is set to 0.170% or less. It is preferably 0.155% or less.
- Si 0.25 to 0.60% Since Si is necessary for deoxidation in steelmaking and is also effective in suppressing the formation of oxide scale after quenching heat treatment, it is contained in an amount of 0.25% or more. If it is less than 0.25%, an oxidation scale is excessively generated, which increases the final polishing load. However, excessive addition suppresses austenite production and impairs hardenability, so the content is set to 0.60% or less.
- Mn 0.10 to 0.60%
- Mn is an austenite-stabilizing element and is necessary for ensuring hardness and the amount of martensite during quenching. Therefore, it is contained in an amount of 0.10% or more. However, in order to promote the formation of oxide scale during quenching and increase the subsequent polishing load, the content is set to 0.60% or less. Further, if it is added excessively, a large amount of MnS is generated and the corrosion resistance is also lowered.
- P 0.035% or less
- P is an element contained as an impurity in alloys such as hot metal and ferrochrome, which are raw materials. Since it is an element harmful to the toughness of the steel sheet after hot spreading annealing and quenching, its content shall be 0.035% or less. Excessive addition reduces hot workability and corrosion resistance.
- S 0.015% or less S has a small solid solubility in the austenite phase and segregates at the grain boundaries to promote a decrease in hot workability. Therefore, the content is set to 0.015% or less. Further, if it is added excessively, a large amount of MnS is generated and the corrosion resistance is also lowered.
- Cr 11.0 to 15.0% Cr is required at least 11.0% or more in order to maintain corrosion resistance as a Western tableware knife. On the other hand, since it also has the effect of narrowing the stable temperature of austenite, it should be 15.0% or less. Preferably, it is 12.0% or more. The upper limit is preferably 14.0% or less. The range is preferably 12.0 to 14.0%.
- Ni 0.05 to 0.60% Like Mn, Ni is an austenite-stable element and is necessary for securing hardness and the amount of martensite during quenching. It also has the effect of improving corrosion resistance. Therefore, it is contained in an amount of 0.05% or more. However, since Ni is more expensive than other elements, it should be 0.60% or less.
- Cu 0.010 to 0.50%
- Cu is an austenite-stable element like Mn and Ni, and is an element that improves corrosion resistance. Although it is an element that cannot be avoided from scrap during steelmaking, it is contained in an amount of 0.010% or more in order to improve corrosion resistance. On the other hand, excessive content reduces hot workability and the like, so the content should be 0.50% or less. Although it is cheaper than Ni, it is relatively expensive, so its addition is an element that we want to keep as low as possible.
- V 0.010 to 0.10%
- V is an element that is often inevitably mixed with ferrochrome or the like, which is an alloy element. The reduction is difficult and contains 0.010% or more. However, since excessive content narrows the austenite formation temperature range, it was set to 0.10% or less. Further, if it is added in an excessive amount, VN is formed and N is immobilized, which causes a decrease in hardness and a decrease in corrosion resistance, which is not preferable.
- Al 0.05% or less Al is an effective element for deoxidation, but its content is 0.05 because excessive content produces CaS, which is a soluble inclusion, during heat spreading and reduces corrosion resistance. % Or less. Al may not be contained.
- N 0.060 to 0.090%
- N is an element that determines quenching hardness together with C, and is an important element in the present invention that improves corrosion resistance. Therefore, in the present invention, the content is 0.060% or more. 0.065% or more is preferable. However, if N is excessively contained, bubble defects are likely to occur in the slab and the production cost is increased in the secondary refining by VOD or the like, so the content is set to 0.090% or less. Preferably, it is 0.085% or less.
- C + 1 / 2N 0.130 to 0.190%
- the elements that determine the hardness of the martensite phase in steel are C and N, the sum of which contributes to the hardness. According to the study of the present inventor, the contribution of N to hardness is half that of C, and it is necessary that C + 1 / 2N is 0.130% or more in order to obtain the hardness required for a Western tableware knife. .. It is preferably 0.150% or more. On the other hand, if C + 1 / 2N is excessive, the quenching hardness is excessively increased, and the toughness of the intermediate material (slab or the like) in the product or manufacturing process is impaired. It is preferably 0.180% or less, and may be 0.175% or less.
- ⁇ p may be adjusted to 130 or more, or 140 or more. In the present invention, it may be 170 or less, and may be 150 or less.
- the steel sheet and steel member of the present invention have a steel composition in which the balance is composed of Fe and impurities.
- elements of Mo, Nb, Ti and Sn, Bi are added in place of a part of Fe in order to improve rust resistance and corrosion resistance. it can.
- Mo 0.01-1.0% Mo is an element that improves corrosion resistance, and its effect is exhibited by adding 0.01% or more. However, Mo is also an expensive element, and even if it is added excessively, the effect is not clear, and the upper limit is 1.0%.
- Ti 0.005 to 0.050%
- Ti is an element that suppresses sensitization and deterioration of corrosion resistance due to precipitation of chromium carbonitride in stainless steel by forming carbonitride. The effect is expressed at 0.005% or more. However, excessive addition destabilizes the martensite phase and reduces the hardness, so the upper limit is 0.050%.
- Nb 0.005 to 0.050%
- Nb is an element that suppresses sensitization and deterioration of corrosion resistance due to precipitation of chromium carbonitride in stainless steel by forming carbonitride. The effect is expressed at 0.005% or more. However, excessive addition destabilizes the martensite phase and reduces the hardness, so the upper limit is 0.050%.
- Sn 0.01% to 0.10% Sn is an element effective for improving corrosion resistance after quenching, preferably 0.01% or more, and preferably 0.05% or more if necessary. However, excessive addition is preferably 0.10% or less because it promotes ear cracking during hot spreading.
- Bi 0.01% to 0.20% Bi is an element that improves corrosion resistance. Although the mechanism has not been clarified, it is considered that the addition of Bi has the effect of miniaturizing MnS, which tends to be the starting point of rusting, and thus reduces the probability of becoming the starting point of rusting. It is effective when added at 0.01% or more. Even if more than 0.20% is added, the effect is only saturated, so the upper limit is set to 0.20%.
- ⁇ ferrite phase ratio of steel plate and steel member The present inventors have found that ⁇ ferrite ( ⁇ Fe) existing in the central portion of the thickness of the steel sheet has a great influence on the end face corrosion resistance of the steel sheet.
- ⁇ ferrite ⁇ Fe
- the grain boundary between ⁇ Fe and the matrix phase ( ⁇ phase) becomes a precipitation site of Cr carbide during cooling, causing sharpening in the vicinity of the precipitated Cr carbide, and end face corrosion resistance. I think it will reduce.
- N improves the end face corrosion resistance is that it also has an effect of suppressing the precipitation of Cr carbides. Therefore, in the present invention, it is effective to suppress ⁇ Fe in steel as well as N content.
- the steel sheet of the present invention is subjected to quenching / tempering treatment and then ⁇ Fe. Evaluate the quantity.
- the quenching conditions for evaluation are heating to 1050 ° C., holding for 30 minutes, and then air cooling, and the tempering conditions are 150 ° C. and 30 minutes.
- the quenching method is air cooling. After quenching and tempering the steel sheet under the above evaluation conditions, good end face corrosion resistance can be obtained if ⁇ Fe is 1% or less when evaluated by the abundance area ratio in the plate thickness cross section. If it is less than 0.1%, excellent corrosion resistance is exhibited regardless of the present invention, but it is not preferable because long-term heat treatment is required to reduce ⁇ Fe and the cost increases. Further, if it exceeds 1%, the improvement of corrosion resistance is not sufficient even with the present invention, and the hardness is also insufficient, which is not preferable. A more preferable upper limit is 0.5%. The range is preferably 0.1% to 0.5%.
- ⁇ Manufacturing method of steel sheet> As the method for producing the steel sheet of the present invention, a conventional method is used. A slab with adjusted components is obtained by melting and casting, which is hot-rolled, then box-annealed, shot, and pickled to obtain a product.
- the slab is preheated.
- heating at 1100 to 1150 ° C. is preferably set to a soaking time of 1 hour or more and 50 hours or less.
- the heating temperature exceeds 1150 ° C.
- the two phases ( ⁇ + ⁇ ) become stable and the amount of ⁇ Fe rapidly increases, which is not preferable.
- the rapidly increased ⁇ Fe remains in a large amount even in the subsequent process, which causes a decrease in hardness.
- ⁇ Fe does not decrease even if it is heated for a long time, which is not preferable.
- the amount of ⁇ Fe is smaller than that in the case of exceeding 1150 ° C., the hardness may be maintained depending on the post-process. Further, if it is less than 1 hour, the amount of ⁇ Fe becomes too large, which is not preferable, and if it exceeds 50 hours, the cost becomes high, which is not preferable.
- This preheating is performed as slab heating before hot rolling, and hot rolling may be performed as it is.
- the obtained steel sheet is punched, hardened, tempered, and polished to prepare a member. After punching, forging is performed and the shape is adjusted.
- the following are preferable conditions for quenching and tempering.
- the quenching temperature is preferably 1000 to 1150 ° C. If it is less than 1000 ° C, the austenite phase is small at high temperature and the hardness after quenching becomes low, which is not preferable. If it is more than 1150 ° C, the ⁇ phase and the stable austenite phase increase, and the hardness also increases in this case. It is not preferable because it decreases.
- the holding time during quenching is preferably 1 minute to 1 hour.
- the cooling rate at the time of quenching is an average cooling rate from the quenching temperature to 600 ° C., preferably 1 ° C./sec or more. If it is less than this, the hardness is lowered, which is not preferable. By air-cooling the quenching, the preferable cooling rate can be realized.
- the tempering is preferably 100 ° C to 250 ° C. If the temperature is lower than 100 ° C, the effect of tempering is poor, and if the temperature exceeds 250 ° C, the decrease in hardness becomes too large, which is not preferable.
- the steels having the composition shown in Tables 1 and 2 were melted and cast into a slab having a thickness of 250 mm.
- these slabs were heat-treated at 1150 ° C. for 40 hours as preheating, and the amount of ⁇ Fe was set within a certain range.
- the A2 steel was preheated at 1175 ° C. for 40 hours and at 950 ° C. for 40 hours to obtain A2'steel and A2'steel, respectively.
- the hot-rolled steel sheet was annealed by box annealing.
- the maximum heating temperature was set to a temperature range of 800 ° C. or higher and 900 ° C. or lower.
- the scale on the surface of the steel sheet after annealing was removed by shot blasting and pickled.
- Example 1 In order to evaluate the obtained steel sheet, a sample for evaluation was cut out from the steel sheet, and the sample was heated to 1050 ° C. for 30 minutes as a quenching / tempering process, held for 30 minutes, and then air-cooled at 150 ° C. for 30 minutes. It was tempered. After that, each evaluation of ⁇ Fe amount measurement, hardness measurement, and end face corrosion resistance was performed. The results obtained are shown in Table 3.
- ⁇ Fe The amount of ⁇ Fe was measured by mirror-polishing and etching the end face of the sample to reveal the structure.
- ⁇ Fe can be expressed in aqua regia or the like as the etching solution, but it is preferable to use a reagent called the improved Murakami reagent described in Non-Patent Document 1 because ⁇ Fe is deeply etched in brown, and evaluation is performed using this. did.
- a typical example is shown in FIG.
- the tissue revealed by the improved Murakami reagent is examined under a microscope, a photograph of ⁇ Fe is taken from the total thickness of a certain width (2 mm in this example), the ⁇ Fe area is obtained from the image analysis, and then the area ratio ( ⁇ Fe area ( ⁇ Fe area ( ⁇ Fe area)). mm 2 ) / 2 mm ⁇ total thickness (mm) ⁇ 100 (%)) was calculated.
- its value needs to be 0.1 to 1%. Further, it is preferably 0.1% to 0.5%.
- ⁇ Fe area ratio 0.1 to 1% was regarded as pass (A), and more than that was regarded as fail (X).
- the surface hardness is evaluated by the Rockwell hardness tester C scale in accordance with JIS Z2245, and 50 or more is passed (A), and the others are rejected (Failure). X).
- the end face corrosion resistance After polishing the sample surface and end face with # 600, the end face is used as the evaluation surface and the salt spray test is performed for 24 hours (JIS Z 2371 "salt spray test method") to determine the rusting point. I counted. A score of 2 or less was regarded as a pass (A), and a score exceeding that score was a failure (X). In particular, those with zero rusting points were regarded as passing (S). Even if the salt spray test was carried out for 24 hours or more, rust did not develop further, so the end face corrosion resistance was judged based on the results for 24 hours.
- All of the steel sheets of the present invention are excellent not only in end face corrosion resistance but also in other properties, and are preferable as steel sheets for Western tableware knives.
- the comparative steel has inferior end face corrosion resistance or inferior other characteristics, and it is clear that it is not preferable as a steel plate for Western tableware knives.
- Example 2 Using the member cut out from the obtained steel sheet, quenching and tempering were performed under the conditions shown in Table 4 to obtain a steel member. Quenching was performed by heating at 1050 to 1150 ° C., and then cooling was performed by controlling the cooling rate from the quenching temperature to 600 ° C. to the cooling rate shown in Table 4. Further, a tempering treatment for 1 to 2 hours was carried out at 150 to 250 ° C. to obtain a steel member. Further, A2'steel and A2'steel were also treated in the same manner.
- Table 4 shows the ⁇ Fe amount measurement, hardness measurement, and end face corrosion resistance evaluation of the obtained steel member together with the heat treatment conditions.
- the evaluation method and evaluation criteria were the same as in Example 1.
- All of the steel members of the present invention are excellent not only in end face corrosion resistance but also in other characteristics, and are preferable as steel members for Western tableware knives.
- the comparative steel has inferior end face corrosion resistance or inferior other characteristics, and it is clear that it is not preferable as a steel member for Western tableware knives.
- the present invention it is possible to produce a martensitic stainless steel member having excellent end face corrosion resistance after air-cooling and quenching with high productivity, and the corrosion resistance of a Western tableware knife produced by using the martensitic stainless steel member is improved, and industrially. , Very useful.
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Abstract
Description
特許文献2には、さらにNを添加した鋼が開示されている。また、特許文献3には、特殊な設備を用いてさらにNを高めた鋼が開示されている。
また、その発銹は焼き入れ時の冷却速度にも依存することを見出した。冷却速度は、焼き入れ設備に大きく依存し変わるものの、焼き入れ温度から炭化物析出が概ね完了する温度である600℃までの平均冷却速度で評価すると、水焼き入れでは100℃/sを超える冷却速度が得られるので、炭化物析出が抑制され発銹は起こりにくいが、テーブルナイフの製造工程で多く用いられる空冷では、その冷却速度が5℃/s程度に過ぎず、炭化物析出が抑制できず発銹が起こりやすいことが分かった。
すなわち、
(1)質量%で、
C:0.100~0.170%、
Si:0.25~0.60%、
Mn:0.10~0.60%、
P:0.035%以下、
S:0.015%以下、
Cr:11.0~15.0%、
Ni:0.05~0.60%、
Cu:0.010~0.50%、
V:0.010~0.10%、
Al:0.05%以下
N:0.060~0.090%
C+1/2N:0.130~0.190%
であり、残部がFeおよび不純物からなる鋼組成を有し、
下記式(1)で示されるγpが120以上であるマルテンサイト系ステンレス鋼板において、
前記マルテンサイト系ステンレス鋼板を1050℃で30分保持後空冷焼き入れし、150℃、30分の焼き戻しを行ったとき、板厚中央部に存在するδフェライト(δFe)の板厚断面における面積率が0.1~1%となることを特徴とするマルテンサイト系ステンレス鋼板。
γp=420C+470N+30Ni+7Mn+9Cu-11.5Cr-11.5Si-12Mo-23V-47Nb-52Al+189 ・・・ 式(1)
式(1)中の元素記号は、当該元素の含有量(質量%)を意味する。
(2)さらに、前記Feの一部に替えて、質量%で、
Mo:0.01~1.0%、
Ti:0.005~0.050%、
Nb:0.005~0.050%
の1種または2種以上を含有することを特徴とする本発明のマルテンサイト系ステンレス鋼板。
(3)さらに、前記Feの一部に替えて、質量%で、
Sn:0.01~0.10%、
Bi:0.01~0.20%
の1種または2種を含有することを特徴とする本発明のマルテンサイト系ステンレス鋼板。
下記式(1)で示されるγpが120以上であり、
さらに、板厚中央部に存在するδフェライト(δFe)の板厚断面における面積率が0.1~1%であることを特徴とするマルテンサイト系ステンレス鋼部材。
γp=420C+470N+30Ni+7Mn+9Cu-11.5Cr-11.5Si-12Mo-23V-47Nb-52Al+189 ・・・ 式(1)
式(1)中の元素記号は、当該元素の含有量(質量%)を意味する。
<鋼板および鋼部材の化学成分>(%は質量%を意味する。)
C:0.100~0.170%
CはNとともに焼き入れ硬さを決める元素であり、洋食器ナイフに必要な硬さを得るためには0.100%以上必要である。好ましくは0.110%以上であり、0.120%以上である。一方、過度に添加すると焼き入れ硬さが必要以上に大きくなり、研磨時の負荷が増えるほか、靱性も低下させる。また、本発明をもってしても空冷焼き入れ時にCr炭化物が析出し耐食性を損なうことも起こりやすくなるため、0.170%以下とする。好ましくは0.155%以下である。
Siは製鋼での脱酸のために必要であるほか、焼き入れ熱処理後の酸化スケールの生成を抑制するにも有効であるため、0.25%以上含有させる。0.25%未満であると酸化スケールが過度に生成し、最終の研磨負荷を増大させる。しかし、過剰の添加はオーステナイト生成を抑制し、焼き入れ性を損ねるために、0.60%以下とする。
Mnはオーステナイト安定元素であり、焼き入れ時の硬さとマルテンサイト量確保のために必要である。そのため、0.10%以上含有させる。しかし、焼き入れ時の酸化スケール生成を促進させ、その後の研磨負荷を増大させるため、0.60%以下とする。また、過剰に添加するとMnSが多く生成し耐食性も低下させる。
Pは原料である溶銑やフェロクロム等の合金中に不純物として含まれる元素である。熱延焼鈍後や焼き入れ後の鋼板の靱性に対して有害な元素であるため、その含有量は0.035%以下とする。過剰に添加すると熱間加工性や耐食性を低下させる。
Sはオーステナイト相に対する固溶度が小さく、粒界に偏析して熱間加工性の低下を促進する。そのため、その含有量を0.015%以下とする。また、過剰に添加するとMnSが多く生成し耐食性も低下させる。
Crは洋食器ナイフとして耐食性を保持するために、少なくとも11.0%以上必要である。一方、オーステナイト安定温度を狭める効果もあるため、15.0%以下とする。好ましくは、12.0%以上である。また上限は14.0%以下が好ましい。範囲としては12.0~14.0%とするのが良い。
Niは、Mnと同様にオーステナイト安定元素であり、焼き入れ時の硬さとマルテンサイト量確保のために必要である。また、耐食性を向上させる効果もある。そのため、0.05%以上含有させる。しかし、Niは他の元素と比較して高価であるため、0.60%以下とする。
Cuは、Mn、Niと同様にオーステナイト安定元素であり、また、耐食性を向上させる元素である。製鋼時のスクラップからの混入が避けられない元素でもあるが、耐食性向上のために、0.010%以上含有させる。一方、過度の含有は熱間加工性等を低下させるので、0.50%以下とする。Niよりは安価であるが比較的高価であるため、その添加はできるだけ低くしたい元素である。
Vは合金元素であるフェロクロム等から不可避的に混入する場合が多い元素である。その削減は困難であり、0.010%以上を含有させる。しかし、過度の含有はオーステナイト形成温度域を狭めるので、0.10%以下とした。また、過剰に添加するとVNを形成し、Nを固定化するため、硬さ低下や耐食性低下を引き起こすため好ましくない。
Alは脱酸のために有効な元素であるが、過度の含有は熱延時に可溶性介在物であるCaSを生成させ、耐食性を低下させるので、その含有は0.05%以下とする。Alは含有しなくても良い。
NはCとともに焼き入れ硬さを決める元素であるとともに、耐食性を向上させる本発明では重要な元素である。そのため、本発明では、0.060%以上含有させる。0.065%以上が好ましい。しかし、Nを過剰に含有させると、スラブ中に気泡欠陥ができやすくなるとともにVOD等による二次精錬では製造コストを増加させるため、その含有量は、0.090%以下とする。好ましくは、0.085%以下である。
鋼中のマルテンサイト相の硬さを決める元素はCとNであり、その合計が硬さに寄与する。本発明者の検討によれば、硬さに対するNの寄与はCの半分であり、洋食器ナイフとして必要な硬さを得るにはC+1/2Nが0.130%以上であることが必要である。好ましくは0.150%以上である。一方、C+1/2Nが過剰になると、焼き入れ硬さが上がりすぎて、製品や製造工程における中間材(鋳片等)の靱性を損ねるために、0.190%以下とする。好ましくは0.180%以下であり、0.175%以下としても良い。
Moは耐食性を向上させる元素であり、0.01%以上の添加でその効果を発現する。しかし、Moは高価な元素でもあり、過度に添加しても効果が明確でなく、1.0%を上限とする。
Tiは、炭窒化物を形成することでステンレス鋼におけるクロム炭窒化物の析出による鋭敏化や耐食性の低下を抑制する元素である。その効果は0.005%以上で発現する。しかし、過度に添加すると、マルテンサイト相を不安定にし、硬さが低下するため、0.050%を上限とする。
Nbは、炭窒化物を形成することでステンレス鋼におけるクロム炭窒化物の析出による鋭敏化や耐食性の低下を抑制する元素である。その効果は0.005%以上で発現する。しかし、過度に添加すると、マルテンサイト相を不安定にし、硬さが低下するため、0.050%を上限とする。
Snは焼入れ後の耐食性向上に有効な元素であり、0.01%以上が好ましく、必要に応じて0.05%以上添加することが好ましい。但し、過度な添加は熱延時の耳割れを促進するため0.10%以下にすることが好ましい。
Biは、耐食性を向上させる元素である。その機構については明確になっていないが、発銹起点となり易いMnSをBi添加により微細化する効果あるため、発銹起点となる確率を低下させると考えている。0.01%以上の添加で効果を発揮する。0.20%超添加しても効果は飽和するだけなので、上限を0.20%とする。
本発明者らは鋼板の板厚中央部に存在するδフェライト(δFe)が鋼板の端面耐食性に大きく影響することを見出した。鋼板を冷却速度の遅い空冷程度で焼き入れた場合、δFeと母相(γ相)との粒界が冷却中のCr炭化物の析出サイトとなり、析出したCr炭化物近傍の鋭敏化を引き起こし、端面耐食性を低下させると考えている。また、Nが端面耐食性を向上させる理由として、Cr炭化物の析出を抑制する効果もあると推定している。
したがって、本発明ではN含有とともに、鋼中のδFeの抑制が有効である。
本発明の鋼板の製造方法は、常法が使用される。溶解・鋳造により、成分が調整されたスラブを得、それを熱間圧延したのち、箱焼鈍を行い、ショット、酸洗して製品とする。
本発明では、得られた鋼板を打ち抜き、焼き入れ、焼き戻しを行い、研磨して部材を作成する。打ち抜き後、鍛造を行い、形を整えることを行う。なお、焼き入れ、焼き戻しの条件として以下が好ましい。焼き入れ温度は1000~1150℃が好ましい。1000℃未満であると、高温時にオーステナイト相が少なく、焼き入れ後の硬さが低くなるため好ましくなく、1150℃超であると、δ相や安定オーステナイト相が増加し、この場合も硬さが低下するため好ましくない。また、焼き入れ時の保持時間は、1分~1時間が好ましい。1分未満であると、高温時にオーステナイト相が少なく、焼き入れ後の硬さが低くなるため好ましくなく、1時間超であると、安定オーステナイト相が増加し、この場合も硬さが低下するため好ましくない。焼き入れ時の冷却速度は、焼き入れ温度から600℃までの平均冷却速度で、1℃/sec以上が好ましい。これ未満であると、硬さが低下するため好ましくない。焼き入れを空冷とすることにより、前記好ましい冷却速度を実現することができる。焼き戻しは、100℃~250℃が好ましい。100℃未満では焼き戻しの効果が乏しく、250℃を超えると、硬さ低下が大きくなりすぎるため、好ましくない。
その後、1150℃に加熱して、熱間圧延を経て板厚3~8mmの熱延鋼板とした。引き続き熱延鋼板の焼鈍を箱焼鈍で行った。最高加熱温度を800℃以上、900℃以下の温度域とした。焼鈍後の鋼板表面のスケールをショットブラストで除去し、酸洗した。
得られた鋼板を評価するため、鋼板から評価用の試料を切り出し、当該試料について、焼き入れ・焼き戻し処理として1050℃に加熱して30分保持した後、空冷し、150℃、30分の焼き戻しを行った。その後、δFe量測定、硬さ測定、端面耐食性の各評価を行った。得られた結果を表3に示す。
得られた鋼板から切り出した部材を用いて、表4に示す条件で焼き入れ焼き戻しを行い、鋼部材とした。焼き入れは1050~1150℃で加熱し、その後焼き入れ温度から600℃までの冷却速度を表4に記載した冷却速度に制御して冷却した。さらに、150~250℃で1~2hの焼き戻し処理を実施して、鋼部材とした。また、A2’鋼、A2”鋼も同様に処理した。
Claims (4)
- 質量%で、
C:0.100~0.170%、
Si:0.25~0.60%、
Mn:0.10~0.60%、
P:0.035%以下、
S:0.015%以下、
Cr:11.0~15.0%、
Ni:0.05~0.60%、
Cu:0.010~0.50%、
V:0.010~0.10%、
Al:0.05%以下
N:0.060~0.090%
C+1/2N:0.130~0.190%
であり、残部がFeおよび不純物からなる鋼組成を有し、
下記式(1)で示されるγpが120以上であるマルテンサイト系ステンレス鋼板において、
前記マルテンサイト系ステンレス鋼板を1050℃で30分保持後空冷焼き入れし、150℃、30分の焼き戻しを行ったとき、板厚中央部に存在するδフェライト(δFe)の板厚断面における面積率が0.1~1%となることを特徴とするマルテンサイト系ステンレス鋼板。
γp=420C+470N+30Ni+7Mn+9Cu-11.5Cr-11.5Si-12Mo-23V-47Nb-52Al+189 ・・・ 式(1)
式(1)中の元素記号は、当該元素の含有量(質量%)を意味する。 - さらに、前記Feの一部に替えて、質量%で、
Mo:0.01~1.0%、
Ti:0.005~0.050%、
Nb:0.005~0.050%
の1種または2種以上を含有することを特徴とする請求項1に記載のマルテンサイト系ステンレス鋼板。 - さらに、前記Feの一部に替えて、質量%で、
Sn:0.01~0.10%、
Bi:0.01~0.20%
の1種または2種を含有することを特徴とする請求項1または請求項2に記載のマルテンサイト系ステンレス鋼板。 - 請求項1~請求項3の何れか1項に記載の鋼組成を有するマルテンサイト系ステンレス鋼部材において、
下記式(1)で示されるγpが120以上であり、
さらに、板厚中央部に存在するδフェライト(δFe)の板厚断面における面積率が0.1~1%であることを特徴とするマルテンサイト系ステンレス鋼部材。
γp=420C+470N+30Ni+7Mn+9Cu-11.5Cr-11.5Si-12Mo-23V-47Nb-52Al+189 ・・・ 式(1)
式(1)中の元素記号は、当該元素の含有量(質量%)を意味する。
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KR102244174B1 (ko) * | 2016-10-18 | 2021-04-26 | 제이에프이 스틸 가부시키가이샤 | 마텐자이트계 스테인리스 강판 |
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2020
- 2020-08-24 CN CN202080054736.0A patent/CN114174546B/zh active Active
- 2020-08-24 EP EP20859662.7A patent/EP4026920A1/en active Pending
- 2020-08-24 WO PCT/JP2020/031886 patent/WO2021044889A1/ja unknown
- 2020-08-24 KR KR1020227002677A patent/KR102670275B1/ko active IP Right Grant
- 2020-08-24 JP JP2021543703A patent/JP7167354B2/ja active Active
- 2020-08-31 TW TW109129777A patent/TWI737475B/zh active
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Also Published As
Publication number | Publication date |
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CN114174546A (zh) | 2022-03-11 |
EP4026920A1 (en) | 2022-07-13 |
JP7167354B2 (ja) | 2022-11-08 |
KR102670275B1 (ko) | 2024-05-30 |
TWI737475B (zh) | 2021-08-21 |
CN114174546B (zh) | 2022-08-30 |
TW202118882A (zh) | 2021-05-16 |
JPWO2021044889A1 (ja) | 2021-03-11 |
KR20220024982A (ko) | 2022-03-03 |
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