CN110527929B - A boron-containing stainless steel plate with excellent plasticity and toughness and preparation method thereof - Google Patents
A boron-containing stainless steel plate with excellent plasticity and toughness and preparation method thereof Download PDFInfo
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- 229910052796 boron Inorganic materials 0.000 title claims abstract description 87
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 title claims abstract description 82
- 239000010935 stainless steel Substances 0.000 title claims abstract description 71
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 71
- 238000002360 preparation method Methods 0.000 title claims abstract description 7
- 238000005096 rolling process Methods 0.000 claims abstract description 60
- 239000002131 composite material Substances 0.000 claims abstract description 54
- 229910000975 Carbon steel Inorganic materials 0.000 claims abstract description 31
- 238000000034 method Methods 0.000 claims abstract description 26
- 239000010962 carbon steel Substances 0.000 claims abstract description 21
- 238000003466 welding Methods 0.000 claims abstract description 17
- 238000005098 hot rolling Methods 0.000 claims abstract description 15
- 238000005266 casting Methods 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 9
- 239000010959 steel Substances 0.000 claims abstract description 9
- 238000002791 soaking Methods 0.000 claims abstract description 8
- 239000000178 monomer Substances 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims abstract 2
- 238000005520 cutting process Methods 0.000 claims abstract 2
- 230000006835 compression Effects 0.000 claims description 19
- 238000007906 compression Methods 0.000 claims description 19
- 239000012535 impurity Substances 0.000 claims description 5
- 238000003801 milling Methods 0.000 claims description 4
- 230000003746 surface roughness Effects 0.000 claims description 4
- 238000009749 continuous casting Methods 0.000 claims description 3
- 238000004512 die casting Methods 0.000 claims description 3
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- 230000001186 cumulative effect Effects 0.000 description 12
- 238000013001 point bending Methods 0.000 description 10
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- 229910052799 carbon Inorganic materials 0.000 description 8
- 239000000203 mixture Substances 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000005238 degreasing Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 239000002915 spent fuel radioactive waste Substances 0.000 description 2
- 238000003860 storage Methods 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
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- 230000003647 oxidation Effects 0.000 description 1
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- 238000004663 powder metallurgy Methods 0.000 description 1
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- 239000002994 raw material Substances 0.000 description 1
- 230000009257 reactivity Effects 0.000 description 1
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Abstract
Description
技术领域technical field
本发明属于冶金材料技术领域，特别涉及一种塑韧性优良的含硼不锈钢厚板及其制备方法。The invention belongs to the technical field of metallurgical materials, and particularly relates to a boron-containing stainless steel thick plate with excellent plasticity and toughness and a preparation method thereof.
背景技术Background technique
作为碳零排放的一种电能，核电发展正在得到全球各国的重视；乏燃料的储存、运输过程，必须使用热中子屏蔽材料降低其反应性，防止重返核临界。天然硼元素中的10B同位素能有效吸收热中子，之后只产生软γ光子和易被吸收的α粒子。将硼元素添加到不锈钢中，所制备出力学及耐蚀性能都较为优良的含硼不锈钢，在核电领域有较为广泛的应用。其中，乏燃料后处理、储存及运输等不同服役环境及条件，对含硼不锈钢的硼含量、厚板及性能均有不同的要求。As a kind of electric energy with zero carbon emission, the development of nuclear power is getting the attention of countries all over the world; during the storage and transportation of spent fuel, thermal neutron shielding materials must be used to reduce its reactivity and prevent it from returning to nuclear criticality. The 10 B isotope in natural boron effectively absorbs thermal neutrons, after which only soft gamma photons and easily absorbed alpha particles are generated. By adding boron element to stainless steel, the boron-containing stainless steel with excellent mechanical and corrosion resistance is prepared, which is widely used in the field of nuclear power. Among them, different service environments and conditions such as spent fuel reprocessing, storage and transportation have different requirements for the boron content, thick plate and performance of boron-containing stainless steel.
不锈钢中添加硼元素后，钢中会析出大量的硬脆的共晶型硼化物，并在奥氏体周围连续分布，不仅恶化坯料的热加工性能，而且导致成品板的室温力学性能尤其是塑性及韧性急剧下降。如果所制备的铸坯厚度增加，凝固组织的尺寸及分布的不均匀性会显著加剧。在后续的轧制过程中，轧件表面到心部区域的轧制力的不均匀传递，导致成品板全厚度方向晶粒、成分很难达到较高的均匀性，最终成品板的力学性能很难满足核电领域服役的要求。After boron is added to stainless steel, a large amount of hard and brittle eutectic boride will be precipitated in the steel, and will be continuously distributed around the austenite, which not only deteriorates the hot workability of the billet, but also leads to the room temperature mechanical properties of the finished plate, especially the plasticity. and toughness dropped sharply. If the thickness of the prepared slab increases, the inhomogeneity of the size and distribution of the solidified structure will be significantly increased. In the subsequent rolling process, the uneven transmission of rolling force from the surface of the rolled piece to the core area makes it difficult to achieve high uniformity of grains and components in the full thickness direction of the finished sheet, and the final finished sheet has very good mechanical properties. It is difficult to meet the requirements of service in the field of nuclear power.
作为目前制备高硼不锈钢板的主要方法，粉末冶金法在制备含硼不锈钢薄板有着独特的技术优势，但是对于含硼不锈钢厚板，由于烧结成型的难度较大，成材率较低，而且制备周期长，制备成本较为昂贵。As the main method for preparing high boron stainless steel plate at present, powder metallurgy has unique technical advantages in preparing boron-containing stainless steel sheet. long and expensive to prepare.
发明内容SUMMARY OF THE INVENTION
针对含硼钢厚板的性能特征及制备技术存在的上述问题，本发明提供了一种塑韧性优良的含硼不锈钢厚板及其制备方法，通过引进复合轧制的方法，提高含硼不锈钢厚板的累积压缩比，获得组织均匀、细小，室温力学性能优良的含硼不锈钢厚板。In view of the performance characteristics of boron-containing steel thick plates and the above problems in the preparation technology, the present invention provides a boron-containing stainless steel thick plate with excellent plasticity and toughness and a preparation method thereof. The cumulative compression ratio of the plate can be obtained to obtain a boron-containing stainless steel plate with a uniform and fine structure and excellent mechanical properties at room temperature.
本发明的塑韧性优良的含硼不锈钢厚板的成分按质量百分比含Cr 18.0～20.0％，Ni 12.0～15.0％，Mn 0.2～2.0％，B 0.5～1.5％，Si＜0.5％，C＜0.02％，其余为Fe和不可避免的杂质元素；其厚度20～80mm，抗拉强度≥550MPa，室温延伸率≥18％，室温冲击韧性≥200 KJ/m2。The composition of the boron-containing stainless steel plate with excellent plasticity and toughness of the present invention contains Cr 18.0-20.0%, Ni 12.0-15.0%, Mn 0.2-2.0%, B 0.5-1.5%, Si<0.5%, C<0.02 according to the mass percentage. %, the rest are Fe and inevitable impurity elements; its thickness is 20-80mm, its tensile strength is ≥550MPa, its room temperature elongation is ≥18%, and its room temperature impact toughness is ≥200 KJ/m 2 .
上述的塑韧性优良的含硼不锈钢厚板中，组织中粒径≤3.0μm的硼化物占全部硼化物总质量20％以上，粒径≥15.0μm的硼化物占全部硼化物总质量5％以下。In the above boron-containing stainless steel plate with excellent plasticity and toughness, the borides with a particle size of ≤3.0 μm in the structure account for more than 20% of the total mass of the total borides, and the borides with a particle size of ≥15.0 μm account for less than 5% of the total mass of the total borides. .
本发明的塑韧性优良的含硼不锈钢厚板的制备方法按以下步骤进行：The preparation method of the boron-containing stainless steel thick plate with excellent plasticity and toughness of the present invention is carried out according to the following steps:
(1)冶炼钢水，然后将钢水通过模铸或连铸制成含硼不锈钢铸坯；含硼不锈钢铸坯的厚度为100～250mm，成分按质量百分比含Cr 18.0～20.0％，Ni 12.0～15.0％，Mn 0.2～2.0％， B 0.5～1.5％，Si≤0.5％，C≤0.02％，其余为Fe和不可避免的杂质元素；(1) Smelting molten steel, and then casting the molten steel into boron-containing stainless steel billet by die casting or continuous casting; the thickness of the boron-containing stainless steel billet is 100-250mm, and the composition contains Cr 18.0-20.0% by mass percentage, Ni 12.0-15.0 %, Mn 0.2～2.0%, B 0.5～1.5%, Si≤0.5%, C≤0.02%, the rest are Fe and inevitable impurity elements;
(2)将含硼不锈钢铸坯放入加热炉随炉升温至均热温度T，并保温90～150min，然后进行多道次粗轧，粗轧终轧温度为900～1000℃，每道次压下量△h1满足10mm≤△h1≤H1mm，得到厚度30～80mm粗轧坯；(2) Put the boron-containing stainless steel billet into the heating furnace and heat up to the soaking temperature T with the furnace, and keep the temperature for 90-150 minutes, then carry out multiple passes of rough rolling, and the final rolling temperature of rough rolling is 900-1000 ° C, and each pass is carried out. The reduction amount Δh 1 satisfies 10mm≤Δh 1 ≤H 1 mm, and a rough rolled billet with a thickness of 30-80mm is obtained;
计算均热温度T所依据的公式按：The formula on which the soaking temperature T is calculated is as follows:
T＝(1155－1450×b)℃ (1)；T=(1155－1450×b)°C (1);
计算H1所依据的公式按： The formula on which H1 is calculated is as follows:
H1＝0.065×Th－1500×b－20 (2)；H 1 =0.065×T h −1500×b−20 (2);
公式(1)和(2)中，Th为每道次的开轧温度，单位℃；b为含硼不锈钢铸坯中硼元素质量百分数，单位％；In formulas (1) and (2), T h is the rolling temperature of each pass, in °C; b is the mass percentage of boron in the boron-containing stainless steel billet, in %;
(3)将粗轧坯铣磨后，在顶面和/或底面的外沿开设用于焊接的V型坡口，再经除油和干燥处理后，制成复合坯单体；将2～3个尺寸相同的复合坯单体上下堆叠并对齐，相邻两个复合坯单体上开设的V型坡口相对，然后置于真空度≤2.0Pa的真空条件下，在V型坡口处将相邻两个复合坯单体焊接，制成复合坯；(3) After milling and grinding the rough rolling billet, a V-shaped groove for welding is opened on the outer edge of the top surface and/or the bottom surface, and after degreasing and drying treatment, a single composite billet is made; Three composite blanks of the same size are stacked up and down and aligned, and the V-shaped grooves opened on two adjacent composite blanks are opposite to each other, and then placed under the vacuum condition of vacuum degree ≤ 2.0Pa, at the V-shaped groove Weld two adjacent composite blanks individually to make a composite blank;
(4)在复合坯的前后两端的端面上分别与一个普碳钢板的端面焊接固定在一起，普碳钢板的宽度与复合坯的宽度相同，普碳钢板的厚度与复合坯的厚度相同，制成组合坯料；(4) The end faces of the front and rear ends of the composite billet are respectively welded and fixed with the end face of a common carbon steel plate. The width of the common carbon steel plate is the same as that of the composite billet, and the thickness of the common carbon steel plate is the same as that of the composite billet. into a composite blank;
(5)将组合坯料加热至1100～1150℃后保温60～150min，然后进行多道次热轧，终轧温度900～1000℃，每道次压下量△h2满足12mm≤△h2≤H2mm，得到厚度20～80mm的热轧板；(5) Heat the composite billet to 1100～1150℃, then keep the temperature for 60～150min, then carry out multi-pass hot rolling, the final rolling temperature is 900～1000℃, and the reduction amount of each pass Δh 2 satisfies 12mm≤Δh 2 ≤ H 2 mm to obtain a hot-rolled sheet with a thickness of 20-80 mm;
计算H2所依据的公式按：The formula on which H2 is calculated is as follows:
H2＝0.07×Th－1500×b－25 (3)；H 2 =0.07×T h −1500×b−25 (3);
公式(3)中，Th为每道次的开轧温度，单位℃；b为含硼不锈钢铸坯中硼元素质量含量，单位％；In formula (3), T h is the rolling temperature of each pass, in °C; b is the mass content of boron in the boron-containing stainless steel billet, in %;
(6)将热轧板前后两端因焊接普碳钢板形成的普碳钢端部切割去除，然后进行固溶处理，固溶处理温度950～1100℃，时间60～150min，再空冷至室温，制成塑韧性优良的含硼不锈钢厚板。(6) Cut and remove the plain carbon steel ends formed by welding plain carbon steel plates at the front and rear ends of the hot-rolled sheet, and then carry out solution treatment. The solution treatment temperature is 950 to 1100°C for 60 to 150 minutes, and then air-cooled to room temperature. Made of boron-containing stainless steel plate with excellent plasticity and toughness.
上述的步骤(2)中，粗轧的压缩比≥2；压缩比计算公式为Hp/Hb，其中Hp为含硼不锈钢铸坯的厚度，Hb为粗轧坯的厚度。In the above step (2), the compression ratio of rough rolling is ≥2; the calculation formula of the compression ratio is H p /H b , where H p is the thickness of the boron-containing stainless steel billet, and H b is the thickness of the rough rolling billet.
上述的步骤(3)中，铣磨至表面粗糙度Ra≤0.8μm。In the above step (3), milling is performed until the surface roughness Ra≤0.8 μm.
上述的步骤(3)中，V型坡口深度3～5mm，角度30～45°。In the above step (3), the depth of the V-shaped groove is 3-5 mm, and the angle is 30-45°.
上述的步骤(3)中，复合坯的宽厚比≥1.2。In the above step (3), the aspect ratio of the composite blank is ≥1.2.
上述的步骤(4)中，普碳钢板的长度为厚度的3～5倍。In the above-mentioned step (4), the length of the ordinary carbon steel plate is 3 to 5 times of the thickness.
上述的步骤(4)中，普碳钢的选用C的质量百分比<0.25％的普碳钢。In the above-mentioned step (4), the ordinary carbon steel with the mass percentage of C <0.25% is selected as the ordinary carbon steel.
上述的步骤(5)中，累积压缩比≥6+200×b；累积压缩比计算公式为Hp×n/Hf，其中Hb为含硼不锈钢铸坯的厚度，n为复合坯的层数(即使用的复合坯单体的个数2～3)，Hf为热轧板的厚度；b为含硼不锈钢铸坯中硼元素质量含量，单位％。In the above step (5), the cumulative compression ratio is ≥6+200×b; the formula for calculating the cumulative compression ratio is H p ×n/H f , where H b is the thickness of the boron-containing stainless steel billet, and n is the layer of the composite billet number (that is, the number of 2-3 composite billet monomers used), H f is the thickness of the hot-rolled sheet; b is the mass content of boron element in the boron-containing stainless steel casting billet, in %.
本发明的原理在于：为了避免铸坯中形成结构复杂的碳硼化物，对含硼不锈钢进行超低碳控制；为了消除铸坯的铸造应力，减少偏析并保证粗轧的顺利进行，铸坯粗轧前需进行长时间；而且由于不锈钢的固相线温度主要与硼含量有关，为了防止过烧，不同的含硼不锈钢铸坯应在不同温度进行保温；为了保证轧制后的坯料不发生边裂，每道次压下量满足特定的公式，并控制终轧温度；在真空度≤2.0Pa的条件下进行真空焊接，形成不间断焊缝，可防止复合坯单体结合界面在焊接、加热及轧制过程发生氧化；在两端焊接普碳钢，防止复合坯料在轧制过程中由于厚度方向的不均匀变形导致分层；为了保证复合坯料既能有效结合又不会发生边裂，控制热轧的每道次；固溶处理可消除复合热轧板的残余应力，同时保证其室温组织更加均匀、稳定。The principle of the invention is as follows: in order to avoid the formation of complex structure carboborides in the slab, ultra-low carbon control is performed on the boron-containing stainless steel; in order to eliminate the casting stress of the slab, reduce segregation and ensure the smooth progress of rough rolling, It takes a long time before rolling; and since the solidus temperature of stainless steel is mainly related to the boron content, in order to prevent over-burning, different boron-containing stainless steel billets should be kept at different temperatures; The reduction amount of each pass satisfies a specific formula, and the final rolling temperature is controlled; vacuum welding is performed under the condition of vacuum degree ≤ 2.0Pa to form an uninterrupted weld, which can prevent the bonding interface of the composite billet from being welded and heated. Oxidation occurs during the rolling process; plain carbon steel is welded at both ends to prevent delamination of the composite billet due to uneven deformation in the thickness direction during the rolling process; in order to ensure that the composite billet can be effectively combined without edge cracking, control Each pass of hot rolling; solution treatment can eliminate the residual stress of the composite hot-rolled sheet, and at the same time ensure that its room temperature structure is more uniform and stable.
另外，控制粗轧压缩比是为了进一步使铸坯中硼化物均匀化和细微化；对其进行表面精加工至表面粗糙度Ra≤0.8μm，之后对精加工后表面进行清洗，去油，保证接触面的平整度和洁净度，使得含硼不锈钢复合坯料在后续的热轧过程中能有效结合起来；为了保证焊接强度，选择加工的V型坡口尺寸；焊接的普碳钢过短，坯料轧制咬入时容易脱落，失去限制作用，过长则会造成原料的浪费，因此需要控制普碳钢的长厚比；为了保证复合坯料中硼化物充分细微化和均匀化分布，控制热轧累积压缩比。In addition, the control of the rough rolling reduction ratio is to further homogenize and miniaturize the boride in the slab; the surface is finished to the surface roughness Ra≤0.8μm, and then the surface after finishing is cleaned and degreasing to ensure that The flatness and cleanliness of the contact surface enable the boron-containing stainless steel composite billets to be effectively combined in the subsequent hot rolling process; in order to ensure the welding strength, the V-shaped groove size for processing is selected; the welded plain carbon steel is too short, and the billet is too short. When rolling, it is easy to fall off and lose its restrictive effect. If it is too long, it will cause waste of raw materials. Therefore, it is necessary to control the length-thickness ratio of ordinary carbon steel. Cumulative compression ratio.
本发明所提供的含硼不锈钢厚板，不仅实现了各层材料的有效结合：三点弯曲、拉伸和冲击等变形过程中，结合界面不发生分层、开裂等状况；而且实现了硼化物分布均匀化和尺寸弥散化的控制。均匀细小的硼化物不仅提高了成品板的均匀变形能力，而且充分发挥第二相粒子的弥散强化作用，最终所制备的含硼不锈钢厚板具有优良的塑性及韧性。The boron-containing stainless steel thick plate provided by the invention not only realizes the effective combination of materials of each layer: in the deformation process such as three-point bending, stretching and impact, the bonding interface does not have delamination and cracking; Control of distribution homogenization and size dispersion. The uniform and fine boride not only improves the uniform deformation ability of the finished plate, but also gives full play to the dispersion strengthening effect of the second phase particles. The final boron-containing stainless steel plate has excellent plasticity and toughness.
与现有技术相比，本发明工艺通过提高含硼不锈钢厚板的累积压缩比，实现了成品板中硼化物的均匀化、细微化控制，有效改善了含硼不锈钢厚板的性能；通过有效控制结合界面精加工、真空焊接、粗轧及复合轧制等过程的工艺参数，保证了各层含硼不锈钢板能有效结合，而且改善了含硼不锈钢厚板的板型和边裂程度，有效提高了含硼不锈钢厚板的成材率；此外，本发明工艺生产流程紧凑，便于实现机械化和自动化，能够显著降低生产能耗和成本。Compared with the prior art, the process of the present invention realizes the homogenization and fine control of boride in the finished plate by increasing the cumulative compression ratio of the boron-containing stainless steel thick plate, and effectively improves the performance of the boron-containing stainless steel thick plate; Controlling the process parameters of bonding interface finishing, vacuum welding, rough rolling and compound rolling ensures that each layer of boron-containing stainless steel plates can be effectively bonded, and improves the shape and edge cracking degree of boron-containing stainless steel thick plates, effectively The yield of the boron-containing stainless steel thick plate is improved; in addition, the process of the invention has a compact production process, is convenient to realize mechanization and automation, and can significantly reduce production energy consumption and cost.
附图说明Description of drawings
图1为本发明的塑韧性优良的含硼不锈钢厚板的制备方法实施例1中步骤(3)～(5) 的部分流程示意图；图中，1、粗轧坯，2、坡口，3、焊缝，4、普碳钢板，5、热轧机轧辊；Fig. 1 is a partial schematic flow chart of steps (3) to (5) in Example 1 of the method for preparing a boron-containing stainless steel plate with excellent plasticity and toughness of the present invention; in the figure, 1, rough rolling, 2, groove, 3 , Welding seam, 4. Plain carbon steel plate, 5. Hot rolling mill roll;
图2为本发明实施例1的塑韧性优良的含硼不锈钢厚板三点弯曲试验失效后的外观形貌照片图；图中，1、裂纹，2、结合界面区域；2 is a photograph of the appearance of the boron-containing stainless steel thick plate with excellent plasticity and toughness in Example 1 of the present invention after the three-point bending test fails; in the figure, 1, crack, 2, bonding interface area;
图3为本发明实施例2的塑韧性优良的含硼不锈钢厚板三点弯曲试验失效后的外观形貌照片图；图中，1、裂纹，2、结合界面区域；3 is a photograph of the appearance and morphology of the boron-containing stainless steel thick plate with excellent plasticity and toughness in Example 2 of the present invention after the failure of the three-point bending test; in the figure, 1, crack, 2, bonding interface area;
图4为本发明对比例2的含硼不锈钢热轧坯料外观照片图。4 is a photograph of the appearance of the boron-containing stainless steel hot-rolled billet of Comparative Example 2 of the present invention.
具体实施方式Detailed ways
本发明制备的粗轧坯为无裂纹粗轧坯。The rough rolled billet prepared by the present invention is a crack-free rough rolled billet.
本发明制备的热轧板为无裂纹热轧板。The hot-rolled sheet prepared by the invention is a crack-free hot-rolled sheet.
本发明的热轧板前后两端是指热轧板长度方向上的两端。The front and rear ends of the hot-rolled sheet in the present invention refer to both ends in the longitudinal direction of the hot-rolled sheet.
本发明实施例中的塑韧性优良的含硼不锈钢厚板的抗拉强度565～690MPa，室温延伸率 19～42％，室温冲击韧性220～530KJ/m2。The boron-containing stainless steel thick plate with excellent plastic toughness in the embodiment of the present invention has a tensile strength of 565-690 MPa, a room temperature elongation of 19-42%, and a room temperature impact toughness of 220-530 KJ/m 2 .
本发明实施例中塑韧性优良的含硼不锈钢厚板中粒径≤3.0μm的硼化物占全部硼化物总质量22～31％，粒径≥15.0μm的硼化物占全部硼化物总质量2.9～4.2％。In the boron-containing stainless steel thick plate with excellent plasticity and toughness in the examples of the present invention, borides with a particle size of ≤3.0 μm account for 22-31% of the total mass of all borides, and borides with a particle size of ≥15.0 μm account for 2.9-31% of the total mass of all borides. 4.2%.
本发明实施例中观测显微组织采用的设备为Olympus BX53M型金相显微镜和JEOLJXA-8530F型电子探针；The equipment used for observing the microstructure in the embodiment of the present invention is an Olympus BX53M metallographic microscope and a JEOLJXA-8530F electron probe;
本发明实施例中室温拉伸试样尺寸及其性能测定方法是依据于GB/T228-2002，所采用的设备为Instron4206-006拉伸实验机。In the embodiment of the present invention, the room temperature tensile sample size and its performance determination method are based on GB/T228-2002, and the equipment used is an Instron4206-006 tensile testing machine.
本发明实施例中室温Charpy-V口冲击试样尺寸及其性能测定方法是依据于 GB-T229-2007，所采用的设备为ZBC2452-B摆锤式冲击试验机。In the embodiment of the present invention, the size of the Charpy-V port impact sample at room temperature and the method for measuring its performance are based on GB-T229-2007, and the equipment used is ZBC2452-B pendulum impact testing machine.
本发明实施例中室温三点弯曲试样尺寸及其性能测定方法是依据GB T 232-2010，所采用的设备为Instron4206-006拉伸实验机。In the embodiment of the present invention, the room temperature three-point bending sample size and its performance measurement method are based on GB T 232-2010, and the equipment used is an Instron4206-006 tensile testing machine.
下面结合实施例，对本发明作进一步地详细说明，但本发明的实施方式不限于此。The present invention will be further described in detail below with reference to the examples, but the embodiments of the present invention are not limited thereto.
本发明实施例中普碳钢的选用C的质量百分比<0.25％的普碳钢。In the embodiment of the present invention, the ordinary carbon steel is selected as the ordinary carbon steel whose mass percentage of C is less than 0.25%.
实施例1Example 1
冶炼钢水，然后将钢水通过模铸或连铸制成含硼不锈钢铸坯；含硼不锈钢铸坯的厚度为 160mm，成分按质量百分比含Cr 18.5％，Ni 14.6％，Mn 0.7％，B 1.25％，Si0.31％，C 0.011 ％，其余为Fe和不可避免的杂质元素；Smelting molten steel, and then casting the molten steel into boron-containing stainless steel billet by die casting or continuous casting; the thickness of the boron-containing stainless steel billet is 160mm, and the composition contains Cr 18.5%, Ni 14.6%, Mn 0.7%, B 1.25% by mass percentage , Si0.31%, C 0.011%, the rest are Fe and inevitable impurity elements;
将含硼不锈钢铸坯放入加热炉随炉升温至均热温度T，并保温120min，然后进行多道次粗轧，粗轧终轧温度为940℃，每道次压下量△h1满足10mm≤△h1≤H1mm，得到厚度65mm粗轧坯；Put the boron-containing stainless steel billet into the heating furnace and heat it up to the soaking temperature T, and keep it for 120 minutes, and then carry out multiple passes of rough rolling. 10mm≤△h 1 ≤H 1 mm to obtain a rough rolled billet with a thickness of 65mm;
T＝(1155－1450×1.25％)＝1137℃；T=(1155－1450×1.25%)=1137℃;
第一道次粗轧时的H1＝0.065×1137－1500×1.25％－20＝74-39＝35mm；H 1 =0.065×1137-1500×1.25%-20=74-39=35mm during the first rough rolling;
粗轧的压缩比160/65＝2.46；The compression ratio of rough rolling is 160/65=2.46;
将粗轧坯铣磨至表面粗糙度Ra≤0.8μm后，在顶面和/或底面的外沿开设用于焊接的V型坡口，再经除油和干燥处理后，制成复合坯单体；将2个尺寸相同的复合坯单体上下堆叠并对齐，相邻两个复合坯单体上开设的V型坡口相对，然后置于真空度≤2.0Pa的真空条件下，在V型坡口处将相邻两个复合坯单体焊接，制成复合坯；其中V型坡口深度4mm，角度45°；复合坯的宽度175mm，厚度130mm，宽厚比1.35；After milling and grinding the rough rolled billet to the surface roughness Ra≤0.8μm, a V-shaped groove for welding is opened on the outer edge of the top surface and/or bottom surface, and after degreasing and drying treatment, a composite billet is made. two composite blanks with the same size are stacked up and down and aligned, and the V-shaped grooves opened on the adjacent two composite blanks are opposite, and then placed under the vacuum condition of vacuum degree ≤ 2.0Pa, in the V-shaped groove The two adjacent composite blanks are welded together at the groove to form a composite blank; the depth of the V-shaped groove is 4mm and the angle is 45°; the width of the composite blank is 175mm, the thickness is 130mm, and the width-thickness ratio is 1.35;
在复合坯的前后两端的端面上分别与一个普碳钢板的端面焊接固定在一起，普碳钢板的宽度与复合坯的宽度相同，普碳钢板的厚度与复合坯的厚度相同，制成组合坯料；普碳钢板的长度450mm，为厚度的3.46倍；The end faces of the front and rear ends of the composite billet are respectively welded and fixed with the end face of a common carbon steel plate. The width of the common carbon steel plate is the same as that of the composite billet, and the thickness of the common carbon steel plate is the same as that of the composite billet. ; The length of ordinary carbon steel plate is 450mm, which is 3.46 times the thickness;
将组合坯料加热至1140℃后保温120min，然后进行多道次热轧，终轧温度930℃，每道次压下量△h2满足12mm≤△h2≤H2mm，得到厚度30mm的热轧板； The composite billet was heated to 1140°C and kept for 120min, and then multi - pass hot rolling was carried out. The final rolling temperature was 930°C. rolled plate;
第一道次热轧时H2＝0.07×1140－1500×1.25％－25＝79.8－18.8－25＝36mm；During the first pass of hot rolling, H 2 =0.07×1140-1500×1.25%-25=79.8-18.8-25=36mm;
累积压缩比160×2/36＝10.67≥6+200×1.25％＝8.5；Cumulative compression ratio 160×2/36=10.67≥6+200×1.25%=8.5;
上述部分步骤的流程如图1所示；The process flow of the above-mentioned part of the steps is shown in Figure 1;
将热轧板前后两端因焊接普碳钢板形成的普碳钢端部切割去除，然后进行固溶处理，固溶处理温度1100℃，时间90min，再空冷至室温，制成塑韧性优良的含硼不锈钢厚板，厚度 30mm，抗拉强度610MPa，室温延伸率24％，室温冲击韧性290KJ/m2；The plain carbon steel ends formed by welding plain carbon steel plates at the front and rear ends of the hot-rolled sheet are cut and removed, and then solution treatment is carried out. Boron stainless steel thick plate, thickness 30mm, tensile strength 610MPa, room temperature elongation 24%, room temperature impact toughness 290KJ/m 2 ;
塑韧性优良的含硼不锈钢厚板中，粒径≤3.0μm的硼化物占全部硼化物总质量24％，粒径≥15.0μm的硼化物占全部硼化物总质量3.8％；In the boron-containing stainless steel plate with excellent plasticity and toughness, borides with particle size ≤3.0μm account for 24% of the total mass of all borides, and borides with particle size ≥15.0μm account for 3.8% of the total mass of borides;
在结合界面区域取厚度为5.0mm的三点弯曲试样进行检测，试样失效后的形貌如图2 所示；拉伸和冲击等变形过程中，结合界面区域2未发生分层、开裂等状况；结合界面能有效结合，且结合强度较高A three-point bending sample with a thickness of 5.0 mm was taken in the bonding interface area for testing. The morphology of the sample after failure is shown in Figure 2; during the deformation process such as tensile and impact, no delamination or cracking occurred in the
实施例2Example 2
方法同实施例1，不同点在于：The method is the same as in Example 1, except that:
(1)含硼不锈钢铸坯的厚度为220mm，成分按质量百分比含Cr 18.2％，Ni 13.4％，Mn 1.15％，B 0.65％，Si 0.23％，C 0.013％；(1) The thickness of boron-containing stainless steel billet is 220mm, and the composition contains Cr 18.2%, Ni 13.4%, Mn 1.15%, B 0.65%, Si 0.23%, C 0.013% by mass percentage;
(2)将含硼不锈钢铸坯放入加热炉随炉升温至均热温度T，并保温120min，然后进行多道次粗轧，粗轧终轧温度为925℃，得到厚度60mm粗轧坯；(2) put the boron-containing stainless steel billet into the heating furnace and be heated to the soaking temperature T with the furnace, and keep the temperature for 120min, then carry out multi-pass rough rolling, and the final rolling temperature of rough rolling is 925 ℃, and obtains the rough rolling billet of thickness 60mm;
T＝(1155－1450×0.65％)＝1146℃；T=(1155－1450×0.65%)=1146℃;
第一道次粗轧时H1＝0.065×1146－1500×0.65％－20＝74.5－9.8-20＝44.7mm；During the first rough rolling, H 1 =0.065×1146-1500×0.65%-20=74.5-9.8-20=44.7mm;
粗轧的压缩比3.67；The compression ratio of rough rolling is 3.67;
(3)将3个复合坯单体堆叠真空焊接制成复合坯；V型坡口深度4mm，角度40°；复合坯的宽度360mm，厚度180mm，宽厚比2；(3) The 3 composite blanks are stacked by vacuum welding to form a composite blank; the depth of the V-shaped groove is 4mm, and the angle is 40°; the width of the composite blank is 360mm, the thickness is 180mm, and the aspect ratio is 2;
(4)普碳钢板的长度550mm，为厚度的3.1倍；(4) The length of ordinary carbon steel plate is 550mm, which is 3.1 times the thickness;
(5)将组合坯料加热至1150℃后保温120min，然后进行多道次热轧，终轧温度955℃，得到厚度75mm的热轧板；(5) heating the composite billet to 1150°C and keeping the temperature for 120min, then performing multiple passes of hot rolling, and the final rolling temperature is 955°C to obtain a hot-rolled sheet with a thickness of 75mm;
第一道次热轧时H2＝0.07×Th－1500×b－25；H 2 =0.07×T h -1500×b-25 during the first pass of hot rolling;
累积压缩比＝220×3/75＝8.8≥6+200×0.65％＝7.4；Cumulative compression ratio=220×3/75=8.8≥6+200×0.65%=7.4;
(6)固溶处理温度1000℃，时间120min；塑韧性优良的含硼不锈钢厚板厚度75mm，抗拉强度565MPa，室温延伸率42％，室温冲击韧性530KJ/m2，粒径≤3.0μm的硼化物占全部硼化物总质量31％，粒径≥15.0μm的硼化物占全部硼化物总质量2.9％；(6) Solution treatment temperature 1000℃, time 120min; thick boron-containing stainless steel plate with excellent plasticity and toughness is 75mm thick, tensile strength 565MPa, room temperature elongation 42%, room temperature impact toughness 530KJ/m 2 , particle size ≤ 3.0μm Borides account for 31% of the total mass of all borides, and borides with a particle size of ≥15.0 μm account for 2.9% of the total mass of all borides;
在结合界面区域取厚度为5.0mm的三点弯曲试样进行检测，试样失效后的形貌如图3 所示，试样弯曲失效时，结合界面区域2未发生分层、开裂，说明含硼不锈钢板热轧后，结合界面能有效结合，且结合强度较高。A three-point bending sample with a thickness of 5.0 mm was taken in the bonding interface area for testing. The morphology of the sample after failure is shown in Figure 3. When the sample fails in bending, no delamination or cracking occurs in the
实施例3Example 3
方法同实施例1，不同点在于：The method is the same as in Example 1, except that:
(1)含硼不锈钢铸坯的厚度为110mm，成分按质量百分比含Cr 19.4％，Ni14.76％， Mn 0.61％，B 1.47％，Si 0.19％，C 0.009％；(1) The thickness of boron-containing stainless steel billet is 110mm, and the composition contains Cr 19.4%, Ni 14.76%, Mn 0.61%, B 1.47%, Si 0.19%, C 0.009% by mass percentage;
(2)将含硼不锈钢铸坯放入加热炉随炉升温至均热温度T，并保温95min，然后进行多道次粗轧，粗轧终轧温度为935℃，得到厚度50mm粗轧坯；(2) put the boron-containing stainless steel casting billet into the heating furnace and be warmed up to the soaking temperature T with the furnace, and keep the temperature for 95min, then carry out multi-pass rough rolling, and the final rolling temperature of rough rolling is 935 ℃, and obtains the rough rolling billet of thickness 50mm;
T＝(1155－1450×1.47％)＝1134℃；T=(1155－1450×1.47%)=1134℃;
第一道次粗轧时H1＝0.065×1134－1500×1.47％－20＝73.7－22.1－20＝31.6mm；During the first rough rolling, H 1 =0.065×1134-1500×1.47%-20=73.7-22.1-20=31.6mm;
粗轧的压缩比2.2；The compression ratio of rough rolling is 2.2;
(3)将2个复合坯单体堆叠真空焊接制成复合坯；V型坡口深度4.5mm，角度45°；复合坯的宽度400mm，厚度100mm，宽厚比4；(3) Two composite blanks are stacked by vacuum welding to form a composite blank; the depth of the V-shaped groove is 4.5mm, and the angle is 45°; the width of the composite blank is 400mm, the thickness is 100mm, and the aspect ratio is 4;
(4)普碳钢板的长度500mm，为厚度的5倍；(4) The length of ordinary carbon steel plate is 500mm, which is 5 times the thickness;
(5)将组合坯料加热至1130℃后保温100min，然后进行多道次热轧，终轧温度920℃，得到厚度20mm的热轧板；(5) heating the composite billet to 1130°C, then keeping the temperature for 100min, and then performing multiple passes of hot rolling, and the final rolling temperature is 920°C to obtain a hot-rolled sheet with a thickness of 20 mm;
第一道次热轧时H2＝0.07×1130－1500×1.47％－25＝79.1－22.1－25＝32mm；During the first pass of hot rolling, H 2 =0.07×1130-1500×1.47%-25=79.1-22.1-25=32mm;
累积压缩比＝110×2/20＝11≥6+200×1.47％＝8.9；Cumulative compression ratio=110×2/20=11≥6+200×1.47%=8.9;
(6)固溶处理温度950℃，时间90min；塑韧性优良的含硼不锈钢厚板厚度20mm，抗拉强度690MPa，室温延伸率19％，室温冲击韧性220KJ/m2，粒径≤3.0μm的硼化物占全部硼化物总质量22％，粒径≥15.0μm的硼化物占全部硼化物总质量4.2％；(6) Solution treatment temperature of 950℃, time of 90min; thick boron-containing stainless steel plate with excellent plasticity and toughness of 20mm in thickness, 690MPa in tensile strength, 19% in room temperature elongation, 220KJ/m 2 in impact toughness at room temperature, and particle size ≤3.0μm Borides account for 22% of the total mass of all borides, and borides with a particle size of ≥15.0 μm account for 4.2% of the total mass of all borides;
在结合界面区域取厚度为5.0mm的三点弯曲试样进行检测，试样弯曲失效时，结合界面区域未发生分层、开裂。A three-point bending sample with a thickness of 5.0 mm was taken in the bonding interface area for testing. When the sample failed to bend, no delamination and cracking occurred in the bonding interface area.
对比例1Comparative Example 1
方法同实施例1，不同点在于：The method is the same as in Example 1, except that:
铸坯粗轧终轧温度为985℃，得到90mm无边裂的粗轧坯，粗轧压缩比为1.78(即将压缩比降低)；The final rolling temperature of the rough rolling of the cast slab is 985°C, and the rough rolling billet with no edge crack of 90mm is obtained, and the rough rolling reduction ratio is 1.78 (that is, the reduction ratio is reduced);
将复合坯料加热至1140℃并保温120min，然后进行热轧，终轧温度为910℃，每道次压下量△h2同实施例1，获得60mm厚无边裂的热轧板，且累积压缩比为5.33(累积压缩比降低)；The composite billet was heated to 1140 ° C and kept for 120 min, and then hot rolled with a final rolling temperature of 910 ° C, and the reduction amount of each pass Δh 2 was the same as that of Example 1, to obtain a 60 mm thick hot-rolled sheet without edge cracks, and the cumulative compression The ratio is 5.33 (the cumulative compression ratio is reduced);
在结合界面区域取厚度为5.0mm的三点弯曲试样进行检测，由于粗轧压缩比较小，粗轧坯中硼化物尺寸仍然较为粗大，且分布不均匀，影响了复合坯料的结合效果；因此，三点弯曲试样失效后，结合界面部分区域发生分层；拉伸和冲击等变形过程中，结合界面部分区域也发生分层、开裂等状况；由于累积压缩比较低，成品板中粒径小于3.0μm的硼化物占比仅为17.5％，粒径大于15.0μm的硼化物占比为7.8％；最终所制备的含硼不锈钢厚板的抗拉强度为～640MPa，室温延伸率为～16.7％，室温冲击韧性为～165KJ/m2。A three-point bending sample with a thickness of 5.0 mm was taken in the bonding interface area for testing. Due to the small compression ratio of rough rolling, the size of boride in the rough rolling billet was still relatively large, and the distribution was uneven, which affected the bonding effect of the composite billet; therefore , after the failure of the three-point bending specimen, delamination occurs in the joint interface area; during the deformation process such as tensile and impact, delamination and cracking also occur in the joint interface part area; due to the relatively low cumulative compression, the particle size in the finished plate The proportion of borides smaller than 3.0 μm is only 17.5%, and the proportion of borides with a particle size larger than 15.0 μm is 7.8%; the tensile strength of the finally prepared boron-containing stainless steel thick plate is ~640MPa, and the room temperature elongation is ~16.7 %, the impact toughness at room temperature is ~165KJ/m 2 .
对比例2Comparative Example 2
方法同实施例1，不同点在于：The method is the same as in Example 1, except that:
在真空度＜2.0Pa的真空条件下进行焊接组坯，得到宽度为175mm的双层复合坯料后；未在复合坯料的两端分别焊接普碳钢；After welding the billet under the vacuum condition of vacuum degree <2.0Pa, after obtaining a double-layer composite billet with a width of 175mm; the ordinary carbon steel was not welded on both ends of the composite billet;
将复合坯料加热、保温后，热轧变形过程中，第二个道次咬入时便脱落，含硼不锈钢热轧坯料外观如图4所示，发生分层，不能有效结合及继续轧制。After the composite billet is heated and kept warm, during the hot rolling deformation process, it will fall off when the second pass bites. The appearance of the boron-containing stainless steel hot-rolled billet is shown in Figure 4, which is delaminated and cannot be effectively combined and continued to be rolled.
对比例3Comparative Example 3
方法同实施例3，不同点在于：The method is the same as in Example 3, except that:
含硼不锈钢铸坯的成分按质量百分比为：Cr 19.1％，Ni 13.5％，Mn 1.78％，B1.61％， Si 0.13％，C 0.015％；其余为Fe和不可避免的杂质元素(即提高了不锈钢中的硼含量)；The composition of boron-containing stainless steel billet by mass percentage is: Cr 19.1%, Ni 13.5%, Mn 1.78%, B1.61%, Si 0.13%, C 0.015%; the rest are Fe and inevitable impurity elements (that is, increase the boron content in stainless steel);
将铸坯粗轧终了温度为945℃，每道次压下量△h1为20mm，由于硼含量B％过高，而且每道次压下量过大，所得到的50mm粗轧坯发生明显边裂；将复合坯料加热、保温、热轧变形后，所得到的厚度为20mm、累积压缩比为11的复合热轧板的边部轻微开裂；The final temperature of rough rolling of the cast slab is 945 °C, and the reduction Δh 1 per pass is 20 mm. Due to the high boron content B% and the excessive reduction per pass, the obtained 50 mm rough rolling billet has obvious occurrence. Edge cracking; after heating, heat preservation and hot rolling deformation of the composite billet, the edge of the obtained composite hot-rolled sheet with a thickness of 20mm and a cumulative compression ratio of 11 was slightly cracked;
经950℃×90min的固溶处理后，获得含硼不锈钢厚板；由于硼含量B％过高，铸坯中的硼化物不仅数量多，而且尺寸较为粗大；经过粗轧变形后尺寸粗大的硼化物占比仍较高，影响了复合坯料的结合效果，因此，三点弯曲试样失效后，结合界面部分区域发生分层；拉伸和冲击等变形过程中，结合界面部分区域也发生分层、开裂等状况；成品板中粒径小于3.0 μm的硼化物占比为14.5％，粒径大于15.0μm的硼化物占比为6.5％；最终所制备的含硼不锈钢厚板的抗拉强度为～715MPa，室温延伸率为～13.3％，室温冲击韧性为～153KJ/m2。After solution treatment at 950℃×90min, a thick boron-containing stainless steel plate is obtained; due to the high boron content B%, the boride in the slab is not only large in quantity, but also relatively large in size; after rough rolling deformation, the boron with large size The proportion of the compound is still high, which affects the bonding effect of the composite billet. Therefore, after the failure of the three-point bending specimen, delamination occurs in part of the bonding interface; during deformation such as tensile and impact, delamination also occurs in part of the bonding interface. , cracking and other conditions; the proportion of boride with particle size less than 3.0 μm in the finished plate is 14.5%, and the proportion of boride with particle size larger than 15.0 μm is 6.5%; the final tensile strength of the boron-containing stainless steel thick plate prepared is ~715MPa, room temperature elongation ~13.3%, room temperature impact toughness ~153KJ/m 2 .
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101875069A (en) * | 2009-11-23 | 2010-11-03 | 北京科技大学 | A short process production method of high boron stainless steel plate |
| CN103614649A (en) * | 2013-12-06 | 2014-03-05 | 东北大学 | High-strength, high-toughness and high-plasticity martensitic stainless steel and preparation method thereof |
| CN105463293A (en) * | 2015-12-02 | 2016-04-06 | 中国核动力研究设计院 | Preparing method of structural shield integration board made of high-boron stainless steel |
| CN106392077A (en) * | 2016-10-09 | 2017-02-15 | 中国核动力研究设计院 | Preparation method for high-boron stainless steel plate |
| CN106702287A (en) * | 2016-12-13 | 2017-05-24 | 东北大学 | Method for improving hot-working performance and room-temperature plasticity of high-boron stainless steel |
| CN106756615A (en) * | 2016-12-13 | 2017-05-31 | 东北大学 | A kind of Short flow method for preparing high-boron stainless steel plate |
| CN108581159A (en) * | 2018-04-28 | 2018-09-28 | 东北大学 | A kind of welding method of thermal neutron shielding stainless steel plate |
| CN110042311A (en) * | 2019-05-30 | 2019-07-23 | 东北大学 | A kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity |
-
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Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101875069A (en) * | 2009-11-23 | 2010-11-03 | 北京科技大学 | A short process production method of high boron stainless steel plate |
| CN103614649A (en) * | 2013-12-06 | 2014-03-05 | 东北大学 | High-strength, high-toughness and high-plasticity martensitic stainless steel and preparation method thereof |
| CN105463293A (en) * | 2015-12-02 | 2016-04-06 | 中国核动力研究设计院 | Preparing method of structural shield integration board made of high-boron stainless steel |
| CN106392077A (en) * | 2016-10-09 | 2017-02-15 | 中国核动力研究设计院 | Preparation method for high-boron stainless steel plate |
| CN106702287A (en) * | 2016-12-13 | 2017-05-24 | 东北大学 | Method for improving hot-working performance and room-temperature plasticity of high-boron stainless steel |
| CN106756615A (en) * | 2016-12-13 | 2017-05-31 | 东北大学 | A kind of Short flow method for preparing high-boron stainless steel plate |
| CN108581159A (en) * | 2018-04-28 | 2018-09-28 | 东北大学 | A kind of welding method of thermal neutron shielding stainless steel plate |
| CN110042311A (en) * | 2019-05-30 | 2019-07-23 | 东北大学 | A kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity |
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