English

• Heterogeneous nanomaterials are considered as one of the most important candidates in widespread applications [1-5]. Considerable attention has been focused on the heterostructure from porous organic framework materials to prepare alloyed, doped, or hybrid nanomaterials for enhanced adsorption or selective performance [6-8]. Metal organic frameworks (MOFs) are connected via organic linkers and metal ions/clusters to form porous frameworks, and have attracted much attention [9-11]. MOFs provide an extensive combination of building units (inorganic nodes and organic linkers) to achieve desired structures and functionalities [12]. Therefore, many efforts have been devoted to prepare MOF-based heterogeneous nanomaterials for enhancing the monomeric performance. Regardless of doping any materials, the new structures and novel properties are generated in the hybrid heterogeneous nanomaterials [13-16]. A growing number of hybrid MOF-based heterogeneous nanomaterials have been prepared and used in various fields.

  Previous studies on hybrid MOF-based heterogeneous nanomaterials mainly focused on relatively single core-shell shape, which leaded to the inability to maximize properties of heterogeneous structures [2,4,17,18]. As one of the most important parameters, the shape of materials usually has significant effect on their performance. The hollow MOFs were successfully fabricated and showed boosted surface area, superb porosity, and excellent pore accessibility, and exhibited a significantly improved performance [19]. Wang et al. reported the dendritic Ag nanocrystals mimicking the structural feature (dendritic) of moth's antennae. The existence of numerous cavity traps in Ag dendritic nanocrystals prolonged reaction time of the gaseous molecules on the surface of solid surface through the "cavity-vortex" effect bring the more sensitive detection sensitivity [20]. A large number of works have verified the positive influence of the shape on material performance [19-22]. But, no works has thus far paid close attention in heterogeneous nanomaterials with the special shapes, which hindered the exploration of controllable design of novel heterogeneous materials complexes.

  Thus, the aim of this work is to provide a viable and versatile strategy for preparing thickness-controllable MOF based hollow nanoflowers with magnetic core (Fe₃O₄@MOFs HFs). Here, the magnetic core hollow nanoflowers (Fe₃O₄ HFs) were firstly synthesizeds. The Fe₃O₄ HFs were employed as the core, metal organic frameworks shell with magnetic core (Fe₃O₄@MOFs HFs) was prepared by liquid phase epitaxy. The thickness of the MOFs shell was randomly controlled by changing the period of assembly. To achieve higher performance, Fe₃O₄@UiO-66-NH₂ HFs were post-modified with Zr⁴⁺ ion to generate Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, which was successfully used to separate and enrich low-abundance phosphopeptides from complex biological samples. This work provides a new avenue for the design and construction of hybrid MOF-based heterogeneous nanomaterials with hollow nanoflower morphology.

  The schematic design of the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs was shown in Scheme 1. Firstly, the precursor hollow nanoflowers (PC HFs) were obtained by the solvothermal reaction with FeCl₃ and urea, and then transformed into Fe₃O₄ HFs after calcination. The polydopamine (PDA) was modified on the surface of Fe₃O₄ HFs, and the NH₂ groups of PDA could react with metal ions (Fe₃O₄@PDA HFs). Then, Fe₃O₄@UiO-66-NH₂ HFs was prepared by the assembling of Fe₃O₄@PDA HFs and MOF stock solution. Finally, the MOF surface was functionalized by -COOH, and Zr⁴⁺ was then immobilized on the material by -COOH. During the process of Zr⁴⁺ immobilization, the coordination interaction between -COOH group and Zr⁴⁺ served as the driving force. Surprisingly, the thickness of the MOFs shell could be controlled by changing the period of assembly.

  Scheme 1

  

  Scheme 1.  The formation processes of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs.

  DownLoad: Full-Size Img PowerPoint

  The structures and morphologies of the prepared materials were thoroughly characterized by scanning electron microscopy (SEM) and transmission electron microscopy (TEM). It was clear that the hollow nanoflowers was organized from nanosheets as building blocks (Figs. 1A, E and I). After a mild heat-treatment was applied on PC HFs, the Fe₃O₄ with thinner and folded nanosheets was obtained (Figs. 1B, F and J). After stirring with PDA, the edges of magnetic nanoflowers were wrapped by the thin layers, which indicated that the PDA was firmly covered on the surface of Fe₃O₄ HFs (Figs. 1C, G and K). The surface of nanopetals were then assembled by a layer of MOF after heated with MOF stock solution for a period of time (Figs. 1D, H and L). From Fig. 1D and Fig. S1 (Supporting information), as the increase of assembly cycles, the thickness of the nanosheets increased until the space between the petals were fully filled up, and then a pure MOF shells were formed on the surface of Fe₃O₄ HFs. Comparing Fig. 1C and Fig. S1A, after one cycle, the thickness of the MOF layer was approximately 80 nm. After another cycle, the thickness of the MOF layer further increased by approximately 163 nm (Fig. S1B). The material that had undergone 5 cycles was completely covered by MOF layer (Figs. S1C and D). Furthermore, the distributions of elements from the area mapping showed a uniform distribution of the metallic distribution of Fe, C and Zr in the Fe₃O₄@UiO-66-NH₂ HFs, which highly indicated that the UiO-66-NH₂ nanoparticles were formed on the surface of Fe₃O₄ HFs and the Fe₃O₄@UiO-66-NH₂ products still kept the hollow structure (Fig. 1M).

  Figure 1

  

  Figure 1.  SEM images of the PC HFs (A), Fe₃O₄ HFs (B), Fe₃O₄@PDA HFs (C), Fe₃O₄@UiO-66-NH₂ HFs (D) with different magnifications. SEM and TEM images for inner hollow structure of PC HFs (E, I), Fe₃O₄ HFs (F, J), Fe₃O₄@PDA HFs (G, K), Fe₃O₄@UiO-66-NH₂ HFs (H, L). (M) Elemental mapping of the Fe₃O₄@UiO-66-NH₂ HFs.

  DownLoad: Full-Size Img PowerPoint

  Fourier transform infrared spectra (FT-IR) of materials were presented in Fig. 2A. Compared with PC, other HFs materials possessed the characteristic peaks (546 cm⁻¹) belonging to Fe-O [23]. Compared with Fe₃O₄ HFs, the new peak appeared at around 1490 cm⁻¹ in Fe₃O₄@PDA HFs, which attributed to the aromatic rings of PDA shell [24]. The FT-IR spectrum of Fe₃O₄@UiO-66-NH₂ obtained after the assembling between the Fe₃O₄@PDA HFs and reaction solution of UiO-66-NH₂. The characteristic peaks appeared at 1651, 1559, 1434, 1385 cm⁻¹ could be ascribed to carboxyl groups stretching modes in the Fe₃O₄@UiO-66-NH₂ [25]. The absorption bands of 1250 and 764 cm⁻¹ were referred to the C–N and N–H stretching bands in the 2-aminoterephthalic acid, confirming the existence of –NH₂ groups [26].

  Figure 2

  

  Figure 2.  (A) FTIR spectra of PC, Fe₃O₄, Fe₃O₄@PDA, Fe₃O₄@UiO-66-NH₂. (B) XRD patterns of PC, Fe₃O₄, UiO-66-NH₂, Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. (C) TGA curves of Fe₃O₄, Fe₃O₄@UiO-66-NH₂, Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. Nitrogen adsorption/desorption isotherms (D) and pore radial distribution (E) of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. (F) Magnetic curves of Fe₃O₄ HFs and Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. XPS spectra of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (G), Zr 3d (H) and N 1s (I).

  DownLoad: Full-Size Img PowerPoint

  In order to further verify the existence of MOF shell and whether post-modification would affect the crystallinity of MOF, X-ray diffractometer (XRD) of PC, Fe₃O₄, UiO-66-NH₂ and Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs were further studied. Compared the spectra of PC and Fe₃O₄ in Fig. 2B, the typical diffraction peaks of Fe₃O₄ (30.2° (220), 35.3° (311), 43.3° (400), 57.1° (511), 62.6° (440)) appeared newly in the Fe₃O₄ spectrum, which indicated the properties of nanomaterials were changed from non-magnetic to magnetic during the high-temperature calcination process. From the spectra of Fe₃O₄, UiO-66-NH₂ and Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, the additional new diffraction peaks at around 7.5° and 25.8° could be assigned to the crystalline structure of the MOFs (UiO-66-NH₂).

  To examine the structural formation, the thermal gravimetric analyser (TGA) of materials were studied (Fig. 2C). Compared with Fe₃O₄, the Fe₃O₄@UiO-66-NH₂ HFs showed extra weight loss of almost 28.0%, indicating that the MOF shell was high yielding. Meanwhile, the TGA analysis of the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs showed the extra weight loss which up to 29.6% compared with the Fe₃O₄. The calculated weight loss of 1.6% was attributed to the post-synthetic modifications of Zr⁴⁺, also indicating that the Zr⁴⁺ groups was high yielding. The large loading yields of MOF and Zr⁴⁺ would help increase performance of the as-prepared materials. The surface area and pore structure were investigated. As shown in Fig. 2D, the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs composites displayed typical IV sorption isotherm profiles with the H4 hysteresis loop at higher pressures that revealed the existence of slit-like mesopore [27]. From Figs. 2D and E, the Brunauer-Emmett-Teller (BET) surface areas and pore size of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs were determined to be 243.60 m²/g and 1.78, 8.55, 14.42 nm, respectively.

  The magnetic curves of the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs and Fe₃O₄ HFs were measured. As shown in Fig. 2F, the saturation magnetization values of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs and Fe₃O₄ HFs were approximately 31.3 and 58.2 emu/g indicating that the surface UiO-66-NH₂-Zr⁴⁺ modification decreased the magnetic properties of original Fe₃O₄ HFs. To obtain detailed elemental compositions and electronic states, X-ray photoelectron spectroscopy (XPS) analysis was further carried out. From Fig. 2G, the survey spectrum of Fe₃O₄ HFs and Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs showed the presence of Fe 2p, C 1s, O 1s and Fe 2p, Zr 3d, C 1s, N 1s, O 1s elements, respectively. As seen from Fig. 2H, the binding peaks at around 182.36 and 184.72 eV were attributed to Zr 3d_5/2 and Zr 3d_3/2, respectively [28]. The binding energy of N 1s emission peak (Fig. 2I) observed at 398.95 and 400.62 eV, which were ascribed to the –NH₂ and –NH₃⁺, respectively. Therefore, the above results obviously confirmed that the formation of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs.

  To demonstrate the feasibility of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs as the affinity platform for enrichment of phosphopeptides, the tryptic digest of the standard phosphoprotein (β-casein) was employed as the testing sample (Fig. 3). Without any pretreatment procedure, the signals were dominated by nonphosphopeptides and only very weak signal intensity of phosphopeptide (β1s) was detected due to the low abundance and serious signal suppression by the nonphosphopeptides (Fig. 3A). Although the signals of phosphopeptide was enhanced after treatment by Fe₃O₄@UiO-66-NH₂ HFs, a number of non-phosphopeptide peaks could still be observed. Otherwise, the relatively high signal-to-noise ratio of the baseline was presented (Fig. 3B). In contrast, after enrichment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, strong signals of phosphopeptide dominated the spectrum and the clean mass spectrometry (MS) background was obtained (Fig. 3C). In addition, three phosphopeptides (β1s, β2s and β3m) and their dephosphopeptide were all detected with strong signals. The details of the phosphopeptides were listed in Table S1 (Supporting information).

  Figure 3

  

  Figure 3.  MALDI-TOF mass spectra of the tryptic digests of β-casein: direct analysis (A), analysis after enrichment with Fe₃O₄@UiO-66-NH₂ HFs (B), analysis after enrichment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (C). “*” and “#” indicate phosphorylated peptides and their dephosphorylated counterparts, respectively.

  DownLoad: Full-Size Img PowerPoint

  To prove that hollow nanoflower structure helped to improve extraction performance, the extraction capacity of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs and Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ NPs for phosphopeptides were compared under the same conditions. From Fig. S2 (Supporting information), after enrichment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, the intensity of the three characteristic signal peaks of the phosphopeptide (β1s, β2s, β3m) were all much higher than that after enrichment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ NPs. Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs showed better enrichment performance might be attributed to the following reasons. Firstly, the hierarchical pores of the special nanoflower structure could more freely allow targets to enter the surface and cavity, providing more accessible sites. Simultaneously, the hollow structure made the active sites inside the material more accessible, ensuring the material properties was used to the greatest extent. Finally, the cavity could hold more targets, accompanied by an increase in adsorption efficiency [29]. The conclusion was summarized that the unique shape of hollow nanoflowers played a crucial role in the selective enrichment of phosphopeptides.

  To investigate selectivity of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs toward phosphopeptides, the tryptic digest mixture of β-casein and bovine serum albumin (BSA) at different molar ratios (1:1000) were used as imitative biological sample. Before enrichment, abundant nonphosphopeptides peaks dominated the chromatogram accompanying with relatively high baseline signal. No any peaks of phosphopeptides were detected, which could be caused by the MS signals of phosphopeptides in the mixture solution (β-casein:BSA=1:1000) were seriously suppressed by the nonphosphopeptides from BSA digest (Fig. S3A in Supporting information). However, after treatment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, three phosphopeptides (m/z = 2061.9, 2566.9 and 3122.6) with high intensities and a relatively clear background were achieved (Fig. S3B in Supporting information), which was better than previously reported materials of MCNC@COF@Zr⁴⁺ (1:200) [30], mSiO₂@PEI (1:100) [31], SiO₂@ATP-Ti⁴⁺ (1:1) [32], Fe₃O₄@C-phosphate-Zr⁴⁺ (1:25) [33], and Fe₃O₄@nSiO₂@mSiO₂/TiO₂-Ti⁴⁺ (1:50) [34]. The results indicated the high selectivity of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs as affinity platform for enrichment of phosphopeptides.

  Considering the special hollow nanoflower structure of material, it was expected that Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs could exclude the large-size interfering substances in the enrichment of phosphopeptides from complex mixture. To test size-exclusion effect, the β-casein digest was mixed with BSA directly at a molar ratio of 1:200 was chosen as a model sample. From Fig. S4C (Supporting information), BSA protein was obviously observed in high molecular weight region without enrichment, while no phosphopeptides could be detected in the low molecular weight region and abundant nonphosphopeptides peaks dominated the chromatogram (Fig. S4A in Supporting information). On the contrary, after treatment by Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, three phosphopeptides with strong intensity were identified (Fig. S4B in Supporting information) and no signal of BSA protein was observed (Fig. S4D in Supporting information). The result indicated that the affinity of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs toward small-size phosphopeptides would be not affected by the large proteins, indicating its potential application in complex biosamples.

  To further explore the sensitivity of the proposed method for the enrichment of phosphopeptides, tryptic digests of β-casein with different concentrations were investigated based on the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (Fig. S5 in Supporting information). Three phosphopeptides were still clearly detected with a relatively high signal (signal-to-noise ratio > 3) even at the concentration as low as 10 fmol (Fig. S5B). Surprisingly, one phosphopeptide peak (β1s) could still be identified when the concentration was as low as 1 fmol (Fig. S5C). The result showed that the prepared material exhibited the better performance than previously reported [30,35-37]. Undoubtedly, Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs had good affinity for phosphopeptides.

  Encouraged by all achieved results, Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs were further applied to capture endogenous phosphopeptide in complex biosamples of human saliva and serum. we had obtained an approval from the Ethics Committee of Biomedical Scientific Research Henan University (HUSOM2024-394). As a widely used clinical sample, human saliva and serum were easy to get and contained many low-abundance endogenous phosphopeptides which could be the potential biomarkers for disease diagnosis. For human serum, without enrichment, nonphosphopeptides dominated the spectrum and no any signal of phosphopeptide could be detected, indicating the interferences were quite seriously (Fig. 4A). On the contrary, after enrichment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs, four phosphopeptides were clearly detected with high intensity (Fig. 4B) and the detailed information of the captured phosphopeptides were listed in Table S2 (Supporting information). For human saliva, before enrichment, also no any phosphopeptide signal was detected, and severe signal suppression with high baseline were found (Fig. 4C). Obviously, after enrichment, 21 endogenous phosphopeptides were detected accompanying the clean baseline signal (Fig. 4D). All peaks were consistent with those reported in the literature [30,38-40]. The enrichment results indicated that the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs could be used as enriched material to capture endogenous phosphopeptides from real biological samples with high efficiency.

  Figure 4

  

  Figure 4.  MALDI-TOF mass spectra of the tryptic digests of human serum and saliva: Direct analysis (A, C) and analysis after enrichment by the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (B, D).

  DownLoad: Full-Size Img PowerPoint

  A general strategy for thickness-controllable synthesis of MOF-based heterogeneous material with special hollow nanoflowers shapes was demonstrated. The thickness could be freely controlled by changing the assembly cycles. The as-prepared MOF-based heterogeneous material possessed the unique hollow nanoflower structure, well-defined hierarchical pores, good superparamagnetic property, large surface area and good hydrophilicity. Furthermore, after post-modification with Zr⁴⁺, the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs showed the ability to selective enrichment of phosphopeptide accompanying with high selectivity, sensitivity and excellent size-exclusion effect. In addition, the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs were successfully applied to specific capture of ultratrace phosphopeptide from complex biosamples. This work will provide a new route for thickness-controllable synthesis of MOF-based heterogeneous material with special hollow nanoflowers shapes, and also shows promising potential in clinical analysis.

  Declaration of competing interest

  The authors declare no competing interests.

  CRediT authorship contribution statement

  Ning Zhang: Conceptualization, Writing – original draft. Mengjie Qin: Data curation. Jiawen Zhu: Investigation, Methodology. Xuejing Lou: Formal analysis, Investigation. Xiao Tian: Data curation, Methodology. Wende Ma: Funding acquisition, Software. Youmei Wang: Validation, Visualization. Minghua Lu: Funding acquisition, Project administration, Writing – review & editing. Zongwei Cai: Writing – review & editing.

  Supplementary materials

  Supplementary material associated with this article can be found, in the online version, at doi:10.1016/j.cclet.2024.110177.

  
  
• 1. [1]

     Y.J. Zhang, P.M. Radjenovic, X.S. Zhou, et al., Adv. Mater. 33 (2021) 2005900. doi: 10.1002/adma.202005900

  2. [2]

     Y. Liu, Y. Yang, Y.J. Sun, et al., J. Am. Chem. Soc. 141 (2019) 7407–7413. doi: 10.1021/jacs.9b01563

  3. [3]

     P.X. Liu, Y. Zhao, R.X. Qin, et al., Science 352 (2016) 797–802. doi: 10.1007/978-3-319-40943-6_123

  4. [4]

     Y. Chen, D. Yang, B.B. Shi, et al., J. Mater. Chem. A 8 (2020) 7724–7732. doi: 10.1039/d0ta00901f

  5. [5]

     M.J. Sailor, J. Park, Adv. Mater. 24 (2012) 3779–3802. doi: 10.1002/adma.201200653

  6. [6]

     R.K. Nutor, Q.P. Cao, R. Wei, et al., Sci. Adv. 7 (2021) 4404. doi: 10.1126/sciadv.abi4404

  7. [7]

     C.A. Witham, W. Huang, C.K. Tsung, et al., Nat. Chem. 2 (2010) 36–41. doi: 10.1038/nchem.468

  8. [8]

     S. Schauermann, N. Nilius, S. Shaikhutdinov, H.J. Freund, Acc. Chem. Res. 46 (2013) 1673–1681. doi: 10.1021/ar300225s

  9. [9]

     B.L. Xue, X.W. Geng, H.H. Cui, et al., Chin. Chem. Lett. 34 (2023) 108140.

  10. [10]

      L.Y. Chen, M. Rong, J.M. Yu, et al., Chem. Eng. J. 457 (2023) 141326.

  11. [11]

      Z.X. Xu, H.L. Chen, H.M. Chu, et al., Chin. Chem. Lett. 34 (2023) 107829. doi: 10.1016/j.cclet.2022.107829

  12. [12]

      H. Liu, Q.Q. Li, P.H. Pan, et al., Chin. Chem. Lett. 34 (2023) 108562.

  13. [13]

      M.Z. Hu, S. Zhao, S.J. Liu, et al., Adv. Mater. 30 (2018) 1801878. doi: 10.1002/adma.201801878

  14. [14]

      J. Yang, F.J. Zhang, X. Wang, et al., Angew. Chem. Int. Ed. 55 (2016) 12854–12858. doi: 10.1002/anie.201604315

  15. [15]

      W. Huang, Q. He, Y.P. Hu, Y.G. Li, Angew. Chem. Int. Ed. 58 (2019) 8676–8680. doi: 10.1002/anie.201900046

  16. [16]

      Z.N. Wang, M.Y. Liu, F. Xiao, Chin. Chem. Lett. 33 (2022) 653–662. doi: 10.3390/machines10080653

  17. [17]

      H.M. Chu, H.Y. Zheng, A.Z. Miao, C.H. Deng, N.R. Sun, Chin. Chem. Lett. 34 (2023) 107716.

  18. [18]

      N.R. Sun, H.L. Yu, Hao Wu, X.Z. Shen, C.H. Deng, TrAC, Trends Anal. Chem. 135 (2021) 116168.

  19. [19]

      Y.X. Sun, K.J. Quan, J. Chen, et al., Chin. Chem. Lett. 34 (2023) 108166.

  20. [20]

      Z. Zhang, W. Yu, J. Wang, et al., Anal. Chem. 89 (2017) 1416–1420. doi: 10.1021/acs.analchem.6b05117

  21. [21]

      C.Y. Tsai, C.H. Chang, T.L. Kao, K.T. Chen, H.Y. Tuan, Chem. Eng. J. 417 (2021) 128552.

  22. [22]

      L. Cao, P.C. Dai, J. Tang, et al., J. Am. Chem. Soc. 142 (2020) 8755–8762. doi: 10.1021/jacs.0c01023

  23. [23]

      R. Wang, H. Qi, H.J. Zheng, Q. Jia, Chin. Chem. Lett. 35 (2024) 109215. doi: 10.1016/j.cclet.2023.109215

  24. [24]

      J.N. Zheng, Z.A. Lin, L. Zhang, H.H. Yang, Sci. China Chem. 58 (2015) 1056–1064. doi: 10.1007/s11426-014-5286-5

  25. [25]

      P.C. Lemaire, D.T. Lee, J.J. Zhao, G.N. Parsons, ACS Appl. Mater. Interfaces 9 (2017) 22042–22054. doi: 10.1021/acsami.7b05214

  26. [26]

      J.M. Wei, W. Zhang, W.Y. Pan, C.R. Li, W.L. Sun, Environ. Sci. Nano. 5 (2018) 1441–1453. doi: 10.1039/c8en00180d

  27. [27]

      Y.F. Shen, Y.W. Zhou, Y.H. Fu, N.Y. Zhang, Renew. Energ. 146 (2020) 1700–1709.

  28. [28]

      L.J. Shen, W.M. Wu, R.W. Liang, R. Lin, L. Wu, Nanoscale 5 (2013) 9374–9382. doi: 10.1039/c3nr03153e

  29. [29]

      J. Yang, F.J. Zhang, H.Y. Lu, et al., Angew. Chem. Int. Ed. 54 (2015) 10889–10893. doi: 10.1002/anie.201504242

  30. [30]

      C.H. Gao, J. Bai, Y.T. He, et al., ACS Appl. Mater. Interfaces 11 (2019) 13735–13741. doi: 10.1021/acsami.9b03330

  31. [31]

      G. -T. Zhu, X. -M. He, S. He, et al., ACS Appl. Mater. Interfaces 8 (2016) 32182–32188. doi: 10.1021/acsami.6b10948

  32. [32]

      H. Wang, Z.X. Tian, J. Chromatogr. A 1564 (2018) 69–75. doi: 10.1007/s11786-018-0330-z

  33. [33]

      D.W. Qi, Y. Mao, J. Lu, C.H. Deng, X.M. Zhang, J. Chromatogr. A 1217 (2010) 2606–2617. doi: 10.1016/j.chroma.2009.10.084

  34. [34]

      D.S. Yang, X.Y. Ding, H. -P. Min, et al., J. Chromatogr. A 1505 (2017) 56–62. doi: 10.1016/j.chroma.2017.05.025

  35. [35]

      H.M. Chu, H.Y. Zheng, N.R. Sun, C.H. Deng, Anal. Chim. Acta 1195 (2022) 338693. doi: 10.1016/j.aca.2021.338693

  36. [36]

      B.D. Zhu, Q. Zhou, D.S. Zhen, et al., Talanta 194 (2019) 870–875. doi: 10.1016/j.talanta.2018.10.073

  37. [37]

      J.Y. Dai, M.D. Wang, H.L. Liu, Talanta 164 (2017) 222–227. doi: 10.1016/j.talanta.2016.11.058

  38. [38]

      H.Z. Lin, H.M. Chen, X. Shao, C.H. Deng, Microchim. Acta 185 (2018) 562. doi: 10.1007/s00604-018-3109-7

  39. [39]

      J. Su, X.W. He, L.X. Chen, Y.K. Zhang, ACS Sustainable Chem. Eng. 6 (2018) 2188–2196. doi: 10.1021/acssuschemeng.7b03607

  40. [40]

      J.W. Wang, Z.D. Wang, N.R. Sun, C.H. Deng, Microchim. Acta 186 (2019) 236. doi: 10.1007/s00604-019-3346-4

• 

  Scheme 1  The formation processes of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs.

  下载: 全尺寸图片 幻灯片
  

  Figure 1  SEM images of the PC HFs (A), Fe₃O₄ HFs (B), Fe₃O₄@PDA HFs (C), Fe₃O₄@UiO-66-NH₂ HFs (D) with different magnifications. SEM and TEM images for inner hollow structure of PC HFs (E, I), Fe₃O₄ HFs (F, J), Fe₃O₄@PDA HFs (G, K), Fe₃O₄@UiO-66-NH₂ HFs (H, L). (M) Elemental mapping of the Fe₃O₄@UiO-66-NH₂ HFs.

  下载: 全尺寸图片 幻灯片
  

  Figure 2  (A) FTIR spectra of PC, Fe₃O₄, Fe₃O₄@PDA, Fe₃O₄@UiO-66-NH₂. (B) XRD patterns of PC, Fe₃O₄, UiO-66-NH₂, Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. (C) TGA curves of Fe₃O₄, Fe₃O₄@UiO-66-NH₂, Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. Nitrogen adsorption/desorption isotherms (D) and pore radial distribution (E) of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. (F) Magnetic curves of Fe₃O₄ HFs and Fe₃O₄@UiO-66-NH₂-Zr⁴⁺. XPS spectra of Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (G), Zr 3d (H) and N 1s (I).

  下载: 全尺寸图片 幻灯片
  

  Figure 3  MALDI-TOF mass spectra of the tryptic digests of β-casein: direct analysis (A), analysis after enrichment with Fe₃O₄@UiO-66-NH₂ HFs (B), analysis after enrichment with Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (C). “*” and “#” indicate phosphorylated peptides and their dephosphorylated counterparts, respectively.

  下载: 全尺寸图片 幻灯片
  

  Figure 4  MALDI-TOF mass spectra of the tryptic digests of human serum and saliva: Direct analysis (A, C) and analysis after enrichment by the Fe₃O₄@UiO-66-NH₂-Zr⁴⁺ HFs (B, D).

  下载: 全尺寸图片 幻灯片
•